Control of polymer architectures by living ring-opening metathesis copolymerization

ABSTRACT

In an aspect, a method of synthesizing a graft copolymer comprises the steps of: copolymerizing a first macromonomer and a first reactive diluent; wherein said first macromonomer comprises a first backbone precursor directly or indirectly covalently linked to a first polymer side chain group; wherein said reactive diluent is provided in the presence of the first macromonomer at an amount selected so as to result in formation said graft copolymer having a first backbone incorporating said diluent and said first macromonomer in a first polymer block characterized by a preselected first graft density or a preselected first graft distribution of said first macromonomer. In some embodiments of this aspect, said preselected first graft density is any value selected from the range of 0.05 to 0.75. In some methods, the composition and amount of said diluent is selected to provide both a first preselected first graft density and a first preselected first graft distribution.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application claims the benefit of and priority to U.S. Provisional Application No. 62/467,925, filed Mar. 7, 2017, which is hereby incorporated in its entirety.

STATEMENT REGARDING FEDERALLY SPONSORED RESEARCH OR DEVELOPMENT

The invention described herein was made with government support under Grant No. DE-AR0000683/T-112546 awarded by the Department of Energy and under Grant No. CHE1502616 awarded by the National Science Foundation. The government has certain rights in the invention.

BACKGROUND OF INVENTION

Molecular architecture impacts the chemical and physical properties of all polymers. Achieving precise control over the chain connectivity, sequence, and symmetry presents synthetic challenges as well as rich opportunities for materials design. Over the past several decades, advances in controlled polymerization have enabled the synthesis of polymers with complex architectures. Graft copolymers are a class of polymer architectures featuring polymeric side chains attached to a polymeric backbone. The grafting density and distribution of grafts along the backbone influence the steric interactions between side chains and in turn influence the physical properties. Graft copolymers display many unique properties compared to their linear analogues, such as extended chain conformations, increased entanglement molecular weights, and architecture-dependent rheological behavior. Additionally, polymers having polymer blocks, such as graft block copolymers, provide platforms for forming useful materials for a wide range of applications, such as photonic materials. Due to their covalently linked yet chemically distinct blocks, block copolymers provide access to a wide range of periodic structures by balancing competing entropic and enthalpic demands. Precise control over polymer sequence and architecture is useful for both understanding structure-property relationships and designing such functional materials.

Despite the importance of grafting density and graft distribution, synthetic strategies that permit precise control of these parameters are currently limited. Grafting-to and grafting-from approaches may require multiple steps in which side chains are either attached to or grown from a pre-formed backbone. Steric congestion along the backbone typically prevents precise control over the molecular weight, grafting density, and side chain distribution. As a result, the synthesis of well-defined architectural variants—let alone materials with variable chemical compositions—is challenging.

Provided herein are a class of graft copolymer and methods for forming them which address these, and other, challenges. Provided herein are also useful functional materials comprising graft copolymers, and methods for forming these functional materials.

SUMMARY OF THE INVENTION

Provided herein are a class of copolymers and methods for making these copolymers. In an embodiment, for example, the invention provides versatile and deterministic methods for making highly tunable graft copolymers having one or more preselected properties. In an embodiment, for example, the invention provides versatile and deterministic methods for making highly tunable graft block copolymers having more than one polymer block at least one of which has one or more preselected properties In an embodiment, for example, the graft copolymers, or polymer block(s) thereof, of the present invention have a preselected graft density, preselected graft distribution, and/or preselected degree of polymerization. The methods and graft copolymers provided herein are compatible with a wide range of polymer side chains, functional groups, and polymer architectures. Also provided herein are self-assembled structures and methods for making the self-assembled structures. The highly tunable and deterministic nature of these graft copolymers and associated methods contributes to the high tunability and versatility of the self-assembled structures, and associated methods, of the present invention. In an embodiment, for example, the self-assembled structures are, or at least partially form, useful functional materials. For example, the self-assembled structures of the invention may be photonic crystals that are capable of, or are configured to, reflect at least a portion of wavelengths in the visible and infrared light range. In an embodiment, for example, methods for forming the self-assembled structures of the invention do not require high-energy or time intensive processes. In an embodiment, for example, the self-assembled structures of the present invention are formed by simple low-pressure annealing or low-temperature annealing. Useful applications of the self-assembled structures of the present invention include, but are not limited to, infrared light-reflecting coatings for windows.

In an aspect, a method of synthesizing a graft copolymer comprises a step of: copolymerizing a first macromonomer and a first reactive diluent; wherein said first macromonomer comprises a first backbone precursor directly or indirectly covalently linked to a first polymer side chain group; wherein said reactive diluent is provided in the presence of the first macromonomer at an amount selected so as to result in formation said graft copolymer having a first backbone incorporating said diluent and said first macromonomer in a first polymer block characterized by a preselected first graft density or a preselected first graft distribution of said first macromonomer.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said preselected first graft density may be any value selected from the range of 0.05 to 0.75. In other words, the diluent and macromonomer and the amount (concentrations) of these may be preselected so as to result in a preselected graft density that is any value in the range of 0.05 to 0.75, such that any graft density in said range is obtainable by the methods according this embodiment.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, the composition and amount of said diluent may be selected to provide both a first preselected first graft density and a first preselected first graft distribution.

Graft copolymers having more than one polymer block (or, graft block copolymer) may be synthesized by some of the methods disclosed herein. Each of the more than one polymer blocks may be a graft copolymer itself, having a respective backbone and respective polymer side chains. At least one of the more than one polymer blocks of a graft (block) copolymer, synthesized according to a method of the present invention, may be a linear polymer block, having no branches. Some of the methods of the present invention allow for tuning each polymer block of the resulting graft (block) copolymer such that each polymer block is characterized by a respective graft density, graft distribution, and/or degree of polymerization. Thus, methods of the present invention are highly versatile.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, the method may further comprise one or more additional copolymerization steps, so as to result in said graft copolymer having one or more additional polymer blocks directly or indirectly covalently linked to said first backbone of said first polymer block.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, the method may further comprise a step of copolymerizing a second polymer block, said second polymer block having a second backbone; wherein said second backbone of said second polymer block is directly or indirectly covalently linked to said first backbone of said first polymer block.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, the method may further comprise a step of copolymerizing a third polymer block, said third polymer block having a third backbone, wherein said third backbone of said third polymer block is directly or indirectly covalently linked to said first backbone of said first polymer block or to said second backbone of said second polymer block. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said third polymer block may comprise one or more third polymer side chain groups, and wherein said third reactive diluent is provided in the presence of the third macromonomer at an amount selected so as to result in formation of said third polymer block characterized by a preselected third graft density or a preselected third graft distribution of said one or more third polymer side chain groups.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said graft copolymer may be a graft block copolymer and the method may further comprise a step of: copolymerizing a second macromonomer and a second reactive diluent; wherein said second macromonomer comprises a second backbone precursor directly or indirectly covalently linked to a second polymer side chain group; wherein said second reactive diluent is provided in the presence of the second macromonomer at an amount selected so as to result in formation said graft copolymer having a second backbone incorporating said second reactive diluent and said second macromonomer in a second polymer block characterized by a preselected second graft density or a preselected second graft distribution of said second macromonomer; wherein said first polymer block and said second polymer block are directly or indirectly covalently linked along said backbone.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said graft copolymer may be a graft block copolymer and the method may further comprise a step of: copolymerizing a second macromonomer and a second reactive diluent; wherein said second macromonomer comprises a second backbone precursor directly or indirectly covalently linked to a second polymer side chain group; thereby resulting in formation of said graft copolymer having a second backbone incorporating said second reactive diluent and said second macromonomer in a second polymer block; wherein said second polymer block is directly or indirectly covalently linked to said first polymer block along said backbone; and wherein said second polymer block has a different composition than said first polymer block. In a further embodiment, said second reactive diluent may be provided in the presence of the second macromonomer at an amount selected so as to result in said second polymer block being characterized by a preselected second graft density or a preselected second graft distribution of said second macromonomer. In a further embodiment, wherein said second polymer side chain group may be different from said first polymer side chain group. In a further embodiment, said second reactive diluent may be different from said first second reactive. In a further embodiment, the method may further comprise a step of copolymerizing a third polymer block, said third polymer block having a third backbone, wherein said third backbone of said third polymer block is directly or indirectly covalently linked to said first backbone of said first polymer block or to said second backbone of said second polymer block; wherein the composition of said third block is different from the composition said first polymer block, said second polymer block or both; and wherein said third polymer block comprises one or more third polymer side chain groups, and wherein said third reactive diluent is provided in the presence of the third macromonomer at an amount selected so as to result in formation of said third polymer block characterized by a preselected third graft density or a preselected third graft distribution of said one or more third polymer side chain groups.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said step of copolymerizing a first macromonomer and a first reactive diluent may be a grafting through copolymerization of said first macromonomer and first reactive diluent. In further embodiments, said grafting through copolymerization of said first macromonomer and first reactive diluent may be carried out via ring-opening metathesis polymerization.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said step of copolymerizing a second macromonomer and a second reactive diluent may be a grafting through copolymerization of said second macromonomer and second reactive diluent. In further embodiments, said grafting through copolymerization of said second macromonomer and second reactive diluent may be carried out via ring-opening metathesis polymerization.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said second polymer side chain group may be different from said first polymer side chain group.

Methods of the present invention allow for a wide range of preselected properties of a graft copolymer, or polymer block(s) thereof. The preselected properties include graft density, graft distribution, and degree of polymerization.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first polymer block may have said preselected first graft density and said preselected first graft distribution of said first macromonomer.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first graft density may be proportional to or equal to [M^(a) ₁]₀/([M^(a) ₁]₀+[M^(a) ₂]₀), where: [M^(a) ₁]₀ and [M^(a) ₂]₀ are initial concentrations of said first macromonomer and said first reactive diluent, respectively. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first graft density may be selected from the range of 0.01 to 0.99. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first graft density may be selected from the range of 0.05 to 0.75. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first graft density may be selected from the range of 0.05 to 0.32, 0.34 to 0.49, 0.51 to 0.65, or 0.68 to 0.75.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first graft density may be equal to [M^(a) ₁]₀/([M^(a) ₁]₀+[M^(a) ₂]₀), where: [M^(a) ₁]₀ and [M^(a) ₂]₀ are initial concentrations of said first macromonomer and said first reactive diluent, respectively. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first graft density may be selected from the range of 0.01 to 0.99. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first graft density may be selected from the range of 0.05 to 0.75. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first graft density may be selected from the range of 0.05 to 0.32, 0.34 to 0.49, 0.51 to 0.65, or 0.68 to 0.75.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first graft distribution may be an alternating graft distribution when r^(a) ₁ is less than 1 and r^(a) ₂ is less than 1; said first graft distribution may be a blocky graft distribution when r^(a) ₁ is greater than 1 and r^(a) ₂ is greater than 1; said first graft distribution may be a random graft distribution when r^(a) ₁ is substantially equal to 1 and r^(a) ₂ is substantially equal to 1; and said first graft distribution may be a gradient graft distribution when r^(a) ₁ is less than 1 and r^(a) ₂ is greater than 1; where: r^(a) ₁ is a reactivity ratio of said first macromonomer; and r^(a) ₂ is a reactivity ratio of said first reactive diluent.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first graft distribution may be an alternating graft distribution when r^(a) ₁ is substantially less than 1 and r^(a) ₂ is substantially less than 1; said first graft distribution may be a blocky graft distribution when r^(a) ₁ is substantially greater than 1 and r^(a) ₂ is substantially greater than 1; said first graft distribution may be a random graft distribution when r^(a) ₁ is substantially equal to 1 and r^(a) ₂ is substantially equal to 1; and said first graft distribution may be a gradient graft distribution when r^(a) ₁ is substantially less than 1 and r^(a) ₂ is substantially greater than 1; where: r^(a) ₁ is a reactivity ratio of said first macromonomer; and r^(a) ₂ is a reactivity ratio of said first reactive diluent.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first graft distribution may be an alternating graft distribution when r^(a) ₁ is substantially less than 1 and r^(a) ₂ is substantially less than 1; said first graft distribution may be a blocky graft distribution when r^(a) ₁ is substantially greater than 1 and r^(a) ₂ is substantially greater than 1; said first graft distribution may be a random graft distribution when r^(a) ₁ is equal to 1 and r^(a) ₂ is substantially to 1; and said first graft distribution may be a gradient graft distribution when r^(a) ₁ is substantially less than 1 and r^(a) ₂ is substantially greater than 1; where: r^(a) ₁ is a reactivity ratio of said first macromonomer; and r^(a) ₂ is a reactivity ratio of said first reactive diluent.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said step of copolymerizing said first macromonomer may be performed in the presence of a catalyst and first polymer block may have a preselected first degree of polymerization, said first degree of polymerization being proportional to or equal to ([M^(a) ₁]₀+[M^(a) ₂]₀)/[Cat]₀; where: [Cat]₀ is an initial concentration of said catalyst.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said step of copolymerizing said first macromonomer may be performed in the presence of a catalyst and first polymer block may have a preselected first degree of polymerization, said first degree of polymerization being equal to ([M^(a) ₁]₀+[M^(a) ₂]₀)/[Cat]₀; where: [Cat]₀ is an initial concentration of said catalyst.

As noted earlier, each polymer block of a graft copolymer synthesized by methods of the present invention may have respective preselected properties.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said second polymer block may have said preselected second graft density and said preselected second graft distribution of said first macromonomer.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said second graft density may be proportional to or equal to [M^(b) ₁]₀/([M^(b) ₁]₀+[M^(b) ₂]₀), where: [M^(b) ₁]₀ and [M^(b) ₂]₀ are initial concentrations of said second macromonomer and said second reactive diluent, respectively.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said preselected second graft density may be any value selected from the range of 0.05 to 0.75. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said second graft density may be selected from the range of 0.01 to 0.99. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said second graft density may be selected from the range of 0.05 to 0.75. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first graft density may be selected from the range of 0.05 to 0.32, 0.34 to 0.49, 0.51 to 0.65, or 0.68 to 0.75.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said second graft distribution may be an alternating graft distribution when r^(b) ₁ is less than 1 and r^(b) ₂ is less than 1; said second graft distribution may be a blocky graft distribution when r^(b) ₁ is greater than 1 and r^(b) ₂ is greater than 1; said second graft distribution may be a random graft distribution when r^(b) ₁ is substantially equal to 1 and r^(b) ₂ is substantially equal to 1; and said second graft distribution may be a gradient graft distribution when r^(b) ₁ is less than 1 and r^(b) ₂ is greater than 1; where: r^(b) ₁ is a reactivity ratio of said second macromonomer; and r^(b) ₂ is a reactivity ratio of said second reactive diluent.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said second graft distribution may be an alternating graft distribution when r^(b) ₁ is substantially less than 1 and r^(b) ₂ is substantially less than 1; said second graft distribution may be a blocky graft distribution when r^(b) ₁ is substantially greater than 1 and r^(b) ₂ is substantially greater than 1; said second graft distribution may be a random graft distribution when r^(b) ₁ is substantially equal to 1 and r^(b) ₂ is substantially equal to 1; and said second graft distribution may be a gradient graft distribution when r^(b) ₁ is substantially less than 1 and r^(b) ₂ is substantially greater than 1; where: r^(b) ₁ is a reactivity ratio of said second macromonomer; and r^(b) ₂ is a reactivity ratio of said second reactive diluent.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said second graft distribution may be an alternating graft distribution when r^(b) ₁ is substantially less than 1 and r^(b) ₂ is substantially less than 1; said second graft distribution may be a blocky graft distribution when r^(b) ₁ is substantially greater than 1 and r^(b) ₂ is substantially greater than 1; said second graft distribution may be a random graft distribution when r^(b) ₁ is equal to 1 and r^(b) ₂ is equal to 1; and said second graft distribution may be a gradient graft distribution when r^(b) ₁ is substantially less than 1 and r^(b) ₂ is substantially greater than 1; where: r^(b) ₁ is a reactivity ratio of said second macromonomer; and r^(b) ₂ is a reactivity ratio of said second reactive diluent.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said step of copolymerizing said second macromonomer may be performed in the presence of a catalyst, and the second polymer block may have a preselected second degree of polymerization, said second degree of polymerization being proportional to or equal to ([M^(b) ₁]₀+[M^(b) ₂]₀)/[Cat]₀; where: [Cat]₀ is an initial concentration of said catalyst.

Additionally, methods of the present invention allow for synthesizing graft copolymers with a low mass dispersity (low polydispersity index), which presents a number of benefits for applications in which the graft copolymers are used.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, a polydispersity index of said graft copolymer may be selected from the range of 1.00 to 1.30. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, a polydispersity index of said graft copolymer may be selected from the range of 1.00 to 1.20. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, a polydispersity index of said graft copolymer may be selected from the range of 1.00 to 1.10.

A wide range of diluents and a wide range of macromonomers are compatible with methods of the present invention for synthesizing graft copolymers. Thus, the graft copolymers of the present invention may have a variety of chemical structures and so a broad set of properties and functionalities that are derived from the obtainable chemical structures of the graft copolymers.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first macromonomer may comprise said first backbone precursor group, one or more anchor groups each covalently linked to said first backbone precursor group, optionally one or more linker groups each covalently linked to an anchor group, and one or more of said first polymer side chain group each covalently linked to an anchor group or a linker group.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first reactive diluent may comprise said first backbone precursor group, one or more anchor groups each covalently linked to said first backbone precursor group, optionally one or more linker groups each covalently linked to an anchor group, and one or more diluent groups each covalently linked to an anchor group or a linker group.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said second macromonomer may comprise said second backbone precursor group, one or more anchor groups each covalently linked to said second backbone precursor group, optionally one or more linker groups each covalently linked to an anchor group, and one or more of said second polymer side chain group each covalently linked to an anchor group or a linker group.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said second reactive diluent may comprise said second backbone precursor group, one or more anchor groups each covalently linked to said first backbone precursor group, optionally one or more linker groups each covalently linked to an anchor group, and one or more diluent groups each covalently linked to an anchor group or a linker group.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first reactive diluent may be defined by the formula (FX1a), (FX1b), or (FX1c):

where: B₁ is said first or said second backbone precursor group having a strained olefin; each A¹ is independently an anchor group having the formula (FX3a) or (FX3b):

each L¹ is independently a linker group selected from the group consisting of a single bond, —O—, C₁-C₁₀ alkyl, C₂-C₁₀ alkenylene, C₃-C₁₀ arylene, C₁-C₁₀ alkoxy, C₁-C₁₀ acyl, triazole, diazole, pyrazole, and any combination thereof; and each D¹ is independently a dangling group that is a substituted or unsubstituted C₁-C₃₀ alkyl, C₃-C₃₀ cycloalkyl, C₅-C₃₀ aryl, C₅-C₃₀ heteroaryl, C₁-C₃₀ acyl, C₁-C₃₀ hydroxyl, C₁-C₃₀ alkoxy, C₂-C₃₀ alkenyl, C₂-C₃₀ alkynyl, C₅-C₃₀ alkylaryl, —CO₂R³, —CONR⁴R⁵, —COR⁶, —SOR⁷, —OSR⁸, —SO₂R⁹, —OR¹⁰, —SR¹¹, —NR¹²R¹³, —NR¹⁴COR¹⁵, C₁-C₃₀ alkyl halide, phosphonate, phosphonic acid, silane, siloxane, silsesquioxane, C₂-C₃₀ halocarbon chain, C₂-C₃₀ perfluorocarbon, C₂-C₃₀ polyethylene glycol, a metal, or a metal complex, wherein each of R³-R¹⁵ is independently H, C₅-C₁₀ aryl or C₁-C₁₀ alkyl.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said second reactive diluent may be defined by the formula (FX1a), (FX1b), or (FX1c):

where:

B1 is said first or said second backbone precursor group having a strained olefin; each A¹ is independently an anchor group having the formula (FX3a) or (FX3b):

each L¹ is independently a linker group selected from the group consisting of a single bond, —O—, C₁-C₁₀ alkyl, C₂-C₁₀ alkenylene, C₃-C₁₀ arylene, C₁-C₁₀ alkoxy, C₁-C₁₀ acyl, triazole, diazole, pyrazole, and any combination thereof; and each D¹ is independently a dangling group that is a substituted or unsubstituted C₁-C₃₀ alkyl, C₃-C₃₀ cycloalkyl, C₅-C₃₀ aryl, C₅-C₃₀ heteroaryl, C₁-C₃₀ acyl, C₁-C₃₀ hydroxyl, C₁-C₃₀ alkoxy, C₂-C₃₀ alkenyl, C₂-C₃₀ alkynyl, C₅-C₃₀ alkylaryl, —CO₂R³, —CONR⁴R⁵, —COR⁶, —SOR⁷, —OSR⁸, —SO₂R⁹, —OR¹⁰, —SR¹¹, —NR¹²R¹³, —NR¹⁴COR¹⁵, C₁-C₃₀ alkyl halide, phosphonate, phosphonic acid, silane, siloxane, silsesquioxane, C₂-C₃₀ halocarbon chain, C₂-C₃₀ perfluorocarbon, C₂-C₃₀ polyethylene glycol, a metal, or a metal complex, wherein each of R³-R¹⁵ is independently H, C₅-C₁₀ aryl or C₁-C₁₀ alkyl.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, each of said first reactive diluent and said second reactive diluent independently may be defined by the formula (FX1a), (FX1b), or (FX1c):

where: B1 is said first or said second backbone precursor group having a strained olefin; each A1 is independently an anchor group having the formula (FX3a) or (FX3b):

each L¹ is independently a linker group selected from the group consisting of a single bond, —O—, C₁-C₁₀ alkyl, C₂-C₁₀ alkenylene, C₃-C₁₀ arylene, C₁-C₁₀ alkoxy, C₁-C₁₀ acyl, triazole, diazole, pyrazole, and any combination thereof; and each D¹ is independently a dangling group that is a substituted or unsubstituted C₁-C₃₀ alkyl, C₃-C₃₀ cycloalkyl, C₅-C₃₀ aryl, C₅-C₃₀ heteroaryl, C₁-C₃₀ acyl, C₁-C₃₀ hydroxyl, C₁-C₃₀ alkoxy, C₂-C₃₀ alkenyl, C₂-C₃₀ alkynyl, C₅-C₃₀ alkylaryl, —CO₂R³, —CONR⁴R⁵, —COR⁶, —SOR⁷, —OSR⁸, —SO₂R⁹, —OR¹⁰, —SR¹¹, —NR¹²R¹³, —NR¹⁴COR¹⁵, C₁-C₃₀ alkyl halide, phosphonate, phosphonic acid, silane, siloxane, silsesquioxane, C₂-C₃₀ halocarbon chain, C₂-C₃₀ perfluorocarbon, C₂-C₃₀ polyethylene glycol, a metal, or a metal complex, wherein each of R³-R¹⁵ is independently H, C₅-C₁₀ aryl or C₁-C₁₀ alkyl.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first diluent may be defined by the formula (FX5):

where: R¹ is —CH₂—, —C₂H₄—, —NH—, or —O—; and each D¹ is independently a C₁-C₄ alkyl dangling group.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said second diluent may be defined by the formula (FX5):

where: R¹ is —CH₂—, —C₂H₄—, —NH—, or —O—; and each D¹ is independently a C₁-C₄ alkyl dangling group.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, each of said first diluent and said second diluent independently may be defined by the formula (FX5):

where R¹ is —CH₂—, —C₂H₄—, —NH—, or —O—; and each D¹ is independently a C₁-C₄ alkyl dangling group.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first macromonomer may be defined by the formula (FX6a), (FX6b), or (FX6c):

where: B1 is said first or said second backbone precursor group having a strained olefin; each A¹ is independently an anchor group having the formula (FX3a) or (FX3b):

each L¹ is independently a linker group selected from the group consisting of a single bond, —O—, C₁-C₁₀ alkyl, C₂-C₁₀ alkenylene, C₃-C₁₀ arylene, C₁-C₁₀ alkoxy, C₁-C₁₀ acyl, triazole, diazole, pyrazole, and any combination thereof; and each P¹ is independently said first or said second polymer side chain group.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said second macromonomer may be defined by the formula (FX6a), (FX6b), or (FX6c):

where: B1 is said first or said second backbone precursor group having a strained olefin; each A¹ is independently an anchor group having the formula (FX3a) or (FX3b):

each L¹ is independently a linker group selected from the group consisting of a single bond, —O—, C₁-C₁₀ alkyl, C₂-C₁₀ alkenylene, C₃-C₁₀ arylene, C₁-C₁₀ alkoxy, C₁-C₁₀ acyl, triazole, diazole, pyrazole, and any combination thereof; and each P¹ is independently said first or said second polymer side chain group.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, each of said first macromonomer and said second macromonomer independently may be defined by the formula (FX6a), (FX6b), or (FX6c):

where: B1 is said first or said second backbone precursor group having a strained olefin; each A¹ is independently an anchor group having the formula (FX3a) or (FX3b):

each L¹ is independently a linker group selected from the group consisting of a single bond, —O—, C₁-C₁₀ alkyl, C₂-C₁₀ alkenylene, C₃-C₁₀ arylene, C₁-C₁₀ alkoxy, C₁-C₁₀ acyl, triazole, diazole, pyrazole, and any combination thereof; and each P¹ is independently said first or said second polymer side chain group.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, B¹ connected to one or more A¹ may have the formula (FX4a), (FX4b), or (FX4c):

where: R¹ is selected from the group consisting of —CH₂—, —C₂H₄—, —NH—, and —O—.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, each L¹ independently may be defined by the formula (FX5a), (FX5b), (FX5c), or any combination thereof:

wherein r is 0 or an integer selected from the range of 1 to 5.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, each P¹ independently may be defined by the formula (FX6a), (FX6b), (FX6c), or (FX6d):

wherein x is an integer selected from the range of 10 to 100; wherein R² is a hydrogen, C₁-C₃₀ alkyl, C₃-C₃₀ cycloalkyl, C₅-C₃₀ aryl, C₅-C₃₀ heteroaryl, C₁-C₃₀ acyl, C₁-C₃₀ hydroxyl, C₁-C₃₀ alkoxy, C₂-C₃₀ alkenyl, C₂-C₃₀ alkynyl, C₅-C₃₀ alkylaryl, —CO₂R³, —CONR⁴R⁵, —COR⁶, —SOR⁷, —OSR⁸, —SO₂R⁹, —OR¹⁰, —SR¹¹, —NR¹²R¹³, —NR¹⁴COR¹⁵, C₁-C₃₀ alkyl halide, phosphonate, phosphonic acid, silane, siloxane, silsesquioxane, C₂-C₃₀ halocarbon chain, C₂-C₃₀ perfluorocarbon, C₂-C₃₀ polyethylene glycol, a metal, or a metal complex, wherein each of R³-R¹⁵ is independently H, C₅-C₁₀ aryl or C₁-C₁₀ alkyl.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said first macromonomer may be defined by the formula (FX7a), (FX7b), or (FX7c):

where: R¹ is selected from the group consisting of —CH₂—, —C₂H₄—, —NH—, and —O—; R² is a hydrogen or C₁-C₅ alkyl; and x is an integer selected from the range of 10 to 100.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said second macromonomer may be defined by the formula (FX7a), (FX7b), or (FX7c):

where: R¹ is selected from the group consisting of —CH₂—, —C₂H₄—, —NH—, and —O—; R² is a hydrogen or C₁-C₅ alkyl; and x is an integer selected from the range of 10 to 100.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, each of said first macromonomer and said second macromonomer independently may be defined by the formula (FX7a), (FX7b), or (FX7c):

where: R¹ is selected from the group consisting of —CH₂—, —C₂H₄—, —NH—, and —O—; R² is a hydrogen or C₁-C₅ alkyl; and x is an integer selected from the range of 10 to 100.

Methods of the present invention are compatible with a broad range of catalysts, solvents, and temperature, for example, which may be selected to synthesize a desired graft copolymer according to methods disclosed herein.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said catalyst may be a fast initiating catalyst. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said catalyst may be a Grubbs' catalyst. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said catalyst may be a third-generation Grubbs' catalyst (“G3”).

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said step of copolymerizing may be performed in the presence of a solvent selected from the group consisting of dichloromethane, dichloroethane, tetrahydrofuran, benzene, toluene, water, ethyl acetate, N,N-dimethylformamide, ethyl acetate, and any combination thereof. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said steps of copolymerizing may be performed in the presence of a solvent selected from the group consisting of dichloromethane, dichloroethane, tetrahydrofuran, benzene, toluene, water, ethyl acetate, N,N-dimethylformamide, ethyl acetate, and any combination thereof.

In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said step of copolymerizing may be performed at a temperature selected from the range of −80° C. to 80° C. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said steps of copolymerizing may be performed at a temperature selected from the range of −80° C. to 80° C. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said step of copolymerizing may be performed at a temperature selected from the range of 0° C. to 30° C. In any embodiment of the methods of synthesizing a graft copolymer disclosed herein, said steps of copolymerizing may be performed at a temperature selected from the range of 0° C. to 30° C.

In an aspect, a method of synthesizing a graft copolymer comprises the steps of: copolymerizing a first macromonomer and a first reactive diluent; wherein said first macromonomer comprises a first backbone precursor directly or indirectly covalently linked to a first polymer side chain group; wherein said copolymerization is a grafting through copolymerization of said first macromonomer and first reactive diluent so as to result in formation said graft copolymer having a first polymer block incorporating said diluent and said first macromonomer and characterized by a first graft density and a first graft distribution of said first macromonomer. In an embodiment of this aspect: (i) said grafting through copolymerization step is carried out via ring-opening metathesis polymerization; and/or (ii) said first reactive diluent is provided in the presence of the first macromonomer at an amount selected so as to result in formation said graft copolymer having said first backbone incorporating said diluent and said first macromonomer in a first polymer block characterized by a preselected first graft density or a preselected first graft distribution of said first macromonomer; and/or (iii) said graft copolymer is a graft block copolymer, and said method further comprises a step of: copolymerizing a second macromonomer and a second reactive diluent; wherein said second macromonomer comprises a second backbone precursor directly or indirectly covalently linked to a second polymer side chain group, thereby resulting in formation said graft copolymer having a second backbone incorporating said second reactive diluent and said second macromonomer in a second polymer block; wherein said second polymer block is directly or indirectly covalently linked to said first polymer block along said backbone; and wherein said second polymer block has a different composition than said first polymer block.

In some embodiments, methods of the present invention may produce any graft copolymer described below.

Provided herein are also graft copolymers, the obtainable properties and parameters of which are highly versatile and tunable.

In an aspect, a graft copolymer comprises a first polymer block comprising at least 10 first repeating units; each of said first repeating units comprising a first polymer backbone group and directly or indirectly covalently linked to a first polymer side chain group; wherein said first polymer block further comprises a first diluent group incorporated into a first backbone of said first polymer block and provided in an amount such that said first polymer block is characterized by a preselected first graft density or a preselected first graft distribution of said first repeating units.

In any embodiment of the graft copolymers disclosed herein, said preselected first graft density may be any value selected from the range of 0.05 to 0.75. In other words, any graft density in said range is obtainable for the graft copolymers of these embodiments.

In any embodiment of the graft copolymers disclosed herein, said first polymer block may be characterized by a preselected first graft density and a preselected first graft distribution of said first repeating units.

Graft copolymers of the present invention may have more than one polymer block. Each of the more than one polymer blocks may be a graft copolymer itself, having a respective backbone and respective polymer side chains. At least one of the more than one polymer blocks of a graft (block) copolymer having no branches. Properties of each polymer block of a graft (block) copolymer may be tunable such that each polymer block is characterized by a respective graft density, graft distribution, and/or degree of polymerization.

In any embodiment of the graft copolymers disclosed herein, the graft copolymer may further comprise one or more additional polymer blocks directly or indirectly covalently linked to said first backbone of said first polymer block.

In any embodiment of the graft copolymers disclosed herein, the graft copolymer may further comprise a second polymer block, said second polymer block having a second backbone; wherein said second backbone of said second polymer block is directly or indirectly covalently linked to said first backbone of said first polymer block.

In any embodiment of the graft copolymers disclosed herein, the graft copolymer may further comprise a third polymer block, said third polymer block having a third backbone, wherein said third backbone of said third polymer block is directly or indirectly covalently linked to said first backbone of said first polymer block or to said second backbone of said second polymer block.

In any embodiment of the graft copolymers disclosed herein, said third polymer block may comprise one or more third polymer side chain groups, and wherein said third polymer block is characterized by a preselected third graft density or a preselected third graft distribution of said one or more third polymer side chain groups.

In any embodiment of the graft copolymers disclosed herein, said graft copolymer may be a graft block copolymer; said graft block copolymer further comprising: a second polymer block comprising at least 10 second repeating units; each of said second repeating unit comprising a second polymer backbone group directly or indirectly covalently linked to a second polymer side chain group; wherein said second polymer block has a second backbone directly or indirectly covalently linked to said first backbone of said first polymer block; and wherein said second polymer block further comprises a second diluent group incorporated into said second backbone of said second polymer block and provided in an amount such that said second polymer block is characterized by a preselected second graft density or a preselected second distribution of said second repeating units.

In any embodiment of the graft copolymers disclosed herein, said second polymer side chain group may be different from said first polymer side chain group.

In any embodiment of the graft copolymers disclosed herein, said second polymer backbone group may be different from said first polymer backbone group.

In any embodiment of the graft copolymers disclosed herein, said second polymer block may be characterized by a preselected second graft density and a preselected second distribution of said second repeating units.

The graft copolymers of the present invention may have a variety of chemical structures, from the chemistry of an individual polymer block to the arrangement of the polymer blocks in a graft copolymer. Thus a broad set of properties and functionalities that are derived from the obtainable chemical structures and arrangements of the graft copolymers

In any embodiment of the graft copolymers disclosed herein, the graft copolymer may be defined by the formula Q¹-[G¹]_(g)-[H¹]_(n)-Q², where: G¹ is said first polymer block having the formula (FX20a), (FX20b), (FX20c), or (FX20d):

[(A′)_(m)-(B′)_(n)]  (FX20a);

[(B′)_(n)-(A′)_(m)]  (FX20b);

[(A′)_(m)-(B′)_(n)-(A′)_(x)]  (FX20d);

[(B′)_(n)-(A′)_(m)-(B′)_(y)]   (FX20d);

H¹ is said second polymer block having the formula (FX30a), (FX30b), (FX30c), or (FX30d):

[(A″)_(q)-(B″)_(s)]  (FX30a);

[(B″)_(s)-(A″)_(q)]  (FX30b);

[(A″)_(q)-(B″)_(s)-(A″)_(u)]  (FX30c);

[(B″)_(s)-(A″)_(q)-(B″)_(v)]   (FX30d);

A′ is said first repeating unit; B′ is a first diluent group; A″ is said second repeating unit; B″ is a second diluent group; Q¹ is a first polymer block terminating group; Q² is a second polymer block terminating group; g is a degree of polymerization of said first polymer block, and g is an integer selected from the range of 10 to 1000; h is a degree of polymerization of said second polymer block, and h is an integer selected from the range of 10 to 1000; each of m and q is independently an integer selected from the range of 10 to 999; each of n and s is independently an integer selected from the range of 1 to 990; each of x and y is independently an integer equal to (g−m−n); and each of u and v is independently an integer equal to (h−q−s); wherein the formulas (FX20a), (FX20b), (FX20c), and (FX20d) indicate amounts of A‘ and B’ which can have any distribution within G¹, and wherein the formulas (FX30a), (FX30b), (FX30c), and (FX30d) indicate amounts of A″ and B″ which can have any distribution within H¹.

In any embodiment of the graft copolymers disclosed herein, each of said first repeating units (e.g., A′) may be defined by the formula (FX10a), (FX10b), (FX10c), (FX11d), (FX11e), (FX11f), (FX11g), (FX11h), or (FX11i):

where: B² is said first or said second backbone precursor group having a strained olefin; each A¹ is independently an anchor group having the formula (FX3a) or (FX3b):

each L¹ is independently a linker group selected from the group consisting of a single bond, —O—, C₁-C₁₀ alkyl, C₂-C₁₀ alkenylene, C₃-C₁₀ arylene, C₁-C₁₀ alkoxy, C₁-C₁₀ acyl, triazole, diazole, pyrazole, and any combination thereof; and each P¹ is independently said first or said second polymer side chain group.

In any embodiment of the graft copolymers disclosed herein, each of said second repeating units (e.g., A″) may be defined by the formula (FX10a), (FX10b), (FX10c), (FX11d), (FX11e), (FX11f), (FX11g), (FX11h), or (FX11i):

where: B² is said first or said second backbone precursor group having a strained olefin; each A¹ is independently an anchor group having the formula (FX3a) or (FX3b):

each L¹ is independently a linker group selected from the group consisting of a single bond, —O—, C₁-C₁₀ alkyl, C₂-C₁₀ alkenylene, C₃-C₁₀ arylene, C₁-C₁₀ alkoxy, C₁-C₁₀ acyl, triazole, diazole, pyrazole, and any combination thereof; and each P¹ is independently said first or said second polymer side chain group.

In any embodiment of the graft copolymers disclosed herein, each of said first repeating units, said second repeating units or both is independently may be defined by the formula (FX10a), (FX10b), (FX10c), (FX11d), (FX11e), (FX11f), (FX11g), (FX11h), or (FX11i):

where: B² is said first or said second backbone precursor group having a strained olefin; each A¹ is independently an anchor group having the formula (FX3a) or (FX3b):

each L¹ is independently a linker group selected from the group consisting of a single bond, —O—, C₁-C₁₀ alkyl, C₂-C₁₀ alkenylene, C₃-C₁₀ arylene, C₁-C₁₀ alkoxy, C₁-C₁₀ acyl, triazole, diazole, pyrazole, and any combination thereof; and each P¹ is independently said first or said second polymer side chain group.

In any embodiment of the graft copolymers disclosed herein, said first diluent group (e.g., B′) (e.g., when incorporated into a polymer backbone) may be defined by the formula (FX11a), (FX11b), (FX11c), (FX11d), (FX11e), (FX11f), (FX11g), (FX11h), or (FX11i):

where: B² is said first or said second backbone precursor group having a strained olefin; each A¹ is independently an anchor group having the formula (FX3a) or (FX3b):

each L¹ is independently a linker group selected from the group consisting of a single bond, —O—, C₁-C₁₀ alkyl, C₂-C₁₀ alkenylene, C₃-C₁₀ arylene, C₁-C₁₀ alkoxy, C₁-C₁₀ acyl, triazole, diazole, pyrazole, and any combination thereof; and each D¹ is independently a dangling group that is a substituted or unsubstituted C₁-C₃₀ alkyl, C₃-C₃₀ cycloalkyl, C₅-C₃₀ aryl, C₅-C₃₀ heteroaryl, C₁-C₃₀ acyl, C₁-C₃₀ hydroxyl, C₁-C₃₀ alkoxy, C₂-C₃₀ alkenyl, C₂-C₃₀ alkynyl, C₅-C₃₀ alkylaryl, —CO₂R³, —CONR⁴R⁵, —COR⁶, —SOR⁷, —OSR⁸, —SO₂R⁹, —OR¹⁰, —SR¹¹, —NR¹²R¹³, —NR¹⁴COR¹⁵, C₁-C₃₀ alkyl halide, phosphonate, phosphonic acid, silane, siloxane, silsesquioxane, C₂-C₃₀ halocarbon chain, C₂-C₃₀ perfluorocarbon, C₂-C₃₀ polyethylene glycol, a metal, or a metal complex, wherein each of R³-R¹⁵ is independently H, C₅-C₁₀ aryl or C₁-C₁₀ alkyl.

In any embodiment of the graft copolymers disclosed herein, said second diluent group (e.g., B″) (e.g., when incorporated into a polymer backbone) may be defined by the formula (FX11a), (FX11b), (FX11c), (FX11d), (FX11e), (FX11f), (FX11g), (FX11h), or (FX11i):

where: B² is said first or said second backbone precursor group having a strained olefin; each A¹ is independently an anchor group having the formula (FX3a) or (FX3b):

each L¹ is independently a linker group selected from the group consisting of a single bond, —O—, C₁-C₁₀ alkyl, C₂-C₁₀ alkenylene, C₃-C₁₀ arylene, C₁-C₁₀ alkoxy, C₁-C₁₀ acyl, triazole, diazole, pyrazole, and any combination thereof; and each D¹ is independently a dangling group that is a substituted or unsubstituted C₁-C₃₀ alkyl, C₃-C₃₀ cycloalkyl, C₅-C₃₀ aryl, C₅-C₃₀ heteroaryl, C₁-C₃₀ acyl, C₁-C₃₀ hydroxyl, C₁-C₃₀ alkoxy, C₂-C₃₀ alkenyl, C₂-C₃₀ alkynyl, C₅-C₃₀ alkylaryl, —CO₂R³, —CONR⁴R⁵, —COR⁶, —SOR⁷, —OSR⁸, —SO₂R⁹, —OR¹⁰, —SR¹¹, —NR¹²R¹³, —NR¹⁴COR¹⁵, C₁-C₃₀ alkyl halide, phosphonate, phosphonic acid, silane, siloxane, silsesquioxane, C₂-C₃₀ halocarbon chain, C₂-C₃₀ perfluorocarbon, C₂-C₃₀ polyethylene glycol, a metal, or a metal complex, wherein each of R³-R¹⁵ is independently H, C₅-C₁₀ aryl or C₁-C₁₀ alkyl.

In any embodiment of the graft copolymers disclosed herein, each of said first diluent groups, said second diluent groups or both (incorporated in a respective polymer backbone) independently may be defined by the formula (FX11a), (FX11b), (FX11c), (FX11d), (FX11e), (FX11f), (FX11g), (FX11h), or (FX11i):

where: B² is said first or said second backbone precursor group having a strained olefin; each A¹ is independently an anchor group having the formula (FX3a) or (FX3b):

each L¹ is independently a linker group selected from the group consisting of a single bond, —O—, C₁-C₁₀ alkyl, C₂-C₁₀ alkenylene, C₃-C₁₀ arylene, C₁-C₁₀ alkoxy, C₁-C₁₀ acyl, triazole, diazole, pyrazole, and any combination thereof; and each D¹ is independently a dangling group that is a substituted or unsubstituted C₁-C₃₀ alkyl, C₃-C₃₀ cycloalkyl, C₅-C₃₀ aryl, C₅-C₃₀ heteroaryl, C₁-C₃₀ acyl, C₁-C₃₀ hydroxyl, C₁-C₃₀ alkoxy, C₂-C₃₀ alkenyl, C₂-C₃₀ alkynyl, C₅-C₃₀ alkylaryl, —CO₂R³, —CONR⁴R⁵, —COR⁶, —SOR⁷, —OSR⁸, —SO₂R⁹, —OR¹⁰, —SR¹¹, —NR¹²R¹³, —NR¹⁴COR¹⁵, C₁-C₃₀ alkyl halide, phosphonate, phosphonic acid, silane, siloxane, silsesquioxane, C₂-C₃₀ halocarbon chain, C₂-C₃₀ perfluorocarbon, C₂-C₃₀ polyethylene glycol, a metal, or a metal complex, wherein each of R³-R¹⁵ is independently H, C₅-C₁₀ aryl or C₁-C₁₀ alkyl.

In any embodiment of the graft copolymers disclosed herein, B² connected to one or more A¹ may have the formula (FX12a), (FX12b), or (FX12c):

In any embodiment of the graft copolymers disclosed herein, each L¹ is independently may be defined by the formula (FX13a), (FX13b), (FX13c), or any combination thereof:

wherein r is 0 or an integer selected from the range of 1 to 5.

In any embodiment of the graft copolymers disclosed herein, each P¹ may be independently defined by the formula (FX14a), (FX14b), (FX14c), or (FX14d):

wherein x is an integer selected from the range of 10 to 100; wherein R² is a hydrogen, C₁-C₃₀ alkyl, C₃-C₃₀ cycloalkyl, C₅-C₃₀ aryl, C₅-C₃₀ heteroaryl, C₁-C₃₀ acyl, C₁-C₃₀ hydroxyl, C₁-C₃₀ alkoxy, C₂-C₃₀ alkenyl, C₂-C₃₀ alkynyl, C₅-C₃₀ alkylaryl, —CO₂R³, —CONR⁴R⁵, —COR⁶, —SOR⁷, —OSR⁸, —SO₂R⁹, —OR¹⁰, —SR¹¹, —NR¹²R¹³, —NR¹⁴COR¹⁵, C₁-C₃₀ alkyl halide, phosphonate, phosphonic acid, silane, siloxane, silsesquioxane, C₂-C₃₀ halocarbon chain, C₂-C₃₀ perfluorocarbon, C₂-C₃₀ polyethylene glycol, a metal, or a metal complex, wherein each of R³-R¹⁵ is independently H, C₅-C₁₀ aryl or C₁-C₁₀ alkyl.

In any embodiment of the graft copolymers disclosed herein, each of said first repeating units (e.g., A′) may be defined by the formula (FX15a), (FX15b), or (FX15c):

where: R¹ is selected from the group consisting of —CH₂—, —C₂H₄—, —NH—, and —O—; R² is a hydrogen or C₁-C₅ alkyl; and x is an integer selected from the range of 10 to 100.

In any embodiment of the graft copolymers disclosed herein, each of said second repeating units (e.g., A″) may be defined by the formula (FX15a), (FX15b), or (FX15c):

where: R¹ is selected from the group consisting of —CH₂—, —C₂H₄—, —NH—, and —O—; R² is a hydrogen or C₁-C₅ alkyl; and x is an integer selected from the range of 10 to 100.

In any embodiment of the graft copolymers disclosed herein, each of said first repeating units, said second repeating units or both is independently may be defined by the formula (FX15a), (FX15b), or (FX15c):

where: R¹ is selected from the group consisting of —CH₂—, —C₂H₄—, —NH—, and —O—; R² is a hydrogen or C₁-C₅ alkyl; and x is an integer selected from the range of 10 to 100.

In any embodiment of the graft copolymers disclosed herein, said first diluent group (e.g., B′) (e.g., when incorporated into a polymer backbone) may be defined by the formula (FX16a), (FX16b), or (FX16c):

In any embodiment of the graft copolymers disclosed herein, said second diluent group (e.g., B″) (e.g., when incorporated into a polymer backbone) may be defined by the formula (FX16a), (FX16b), or (FX16c):

In any embodiment of the graft copolymers disclosed herein, each of said first diluent groups, said second diluent groups or both is independently may be defined by the formula (FX16a), (FX16b), or (FX16c):

Graft copolymers of the present invention may be characterized by a subset of a wide range of preselected properties. Moreover, each polymer block of a graft copolymer having more than one polymer block may be characterized by a subset of a wide range of preselected properties. Preselected properties include graft density, graft distribution, and degree of polymerization.

In any embodiment of the graft copolymers disclosed herein, said first graft density may be proportional to or equal to [M^(a) ₁]₀/([M^(a) ₁]₀+[M^(a) ₂]₀), where: [M^(a) ₁]₀ and [M^(a) ₂]₀ are initial concentrations of said first macromonomer and said first diluent group, respectively. In any embodiment of the graft copolymers disclosed herein, said first graft density may be selected from the range of 0.01 to 0.99. In any embodiment of the graft copolymers disclosed herein, first graft density may be selected from the range of 0.05 to 0.75. In any embodiment of the graft copolymers disclosed herein, said first graft density may be selected from the range of 0.05 to 0.32, 0.34 to 0.49, 0.51 to 0.65, or 0.68 to 0.75.

In any embodiment of the graft copolymers disclosed herein, said first graft density may be equal to [M^(a) ₁]₀/([M^(a) ₁]₀+[M^(a) ₂]₀), where: [M^(a) ₁]₀ and [M^(a) ₂]₀ are initial concentrations of said first macromonomer and said first diluent group, respectively. In any embodiment of the graft copolymers disclosed herein, said first graft density may be selected from the range of 0.01 to 0.99. In any embodiment of the graft copolymers disclosed herein, first graft density may be selected from the range of 0.05 to 0.75. In any embodiment of the graft copolymers disclosed herein, said first graft density may be selected from the range of 0.05 to 0.32, 0.34 to 0.49, 0.51 to 0.65, or 0.68 to 0.75.

In any embodiment of the graft copolymers disclosed herein, said first graft distribution may be an alternating graft distribution when r^(a) ₁ is less than 1 and r^(a) ₂ is less than 1; said first graft distribution may be a blocky graft distribution when r^(a) ₁ is greater than 1 and r^(a) ₂ is greater than 1; said first graft distribution may be a random graft distribution when r^(a) ₁ is substantially equal to 1 and r^(a) ₂ is substantially equal to 1; and said first graft distribution may be a gradient graft distribution when r^(a) ₁ is less than 1 and r^(a) ₂ is greater than 1; where: r^(a) ₁ is a reactivity ratio of said first macromonomer; and r^(a) ₂ is a reactivity ratio of said first diluent group (or first reactive diluent).

In any embodiment of the graft copolymers disclosed herein, said first graft distribution may be an alternating graft distribution when r^(a) ₁ is substantially less than 1 and r^(a) ₂ is substantially less than 1; said first graft distribution may be a blocky graft distribution when r^(a) ₁ is substantially greater than 1 and r^(a) ₂ is substantially greater than 1; said first graft distribution may be a random graft distribution when r^(a) ₁ is substantially equal to 1 and r^(a) ₂ is substantially equal to 1; and said first graft distribution may be a gradient graft distribution when r^(a) ₁ is substantially less than 1 and r^(a) ₂ is substantially greater than 1; where: r^(a) ₁ is a reactivity ratio of said first macromonomer; and r^(a) ₂ is a reactivity ratio of said first diluent group (or first reactive diluent).

In any embodiment of the graft copolymers disclosed herein, said first graft distribution may be an alternating graft distribution when r^(a) ₁ is substantially less than 1 and r^(a) ₂ is substantially less than 1; said first graft distribution may be a blocky graft distribution when r^(a) ₁ is substantially greater than 1 and r^(a) ₂ is substantially greater than 1; said first graft distribution may be a random graft distribution when r^(a) ₁ is equal to 1 and r^(a) ₂ is equal to 1; and said first graft distribution may be a gradient graft distribution when r^(a) ₁ is substantially less than 1 and r^(a) ₂ is substantially greater than 1; where: r^(a) ₁ is a reactivity ratio of said first macromonomer; and r^(a) ₂ is a reactivity ratio of said first diluent group (or first reactive diluent).

In any embodiment of the graft copolymers disclosed herein, said step of copolymerizing said first macromonomer may be performed in the presence of a catalyst. In any embodiment of the graft copolymers disclosed herein, the first polymer block may have a preselected first degree of polymerization, said first degree of polymerization being proportional to or equal to ([M^(a) ₁]₀+[M^(a) ₂]₀)/[Cat]₀; where: [Cat]₀ is initial concentration of said catalyst.

In any embodiment of the graft copolymers disclosed herein, said second graft density is proportional to or equal to [M^(b) ₁]₀/([M^(b) ₁]₀+[M^(b) ₂]₀), where: [M^(b) ₁]₀ and [M^(b) ₂]₀ are initial concentrations of said second macromonomer and said second diluent group, respectively. In any embodiment of the graft copolymers disclosed herein, said second graft density may be selected from the range of 0.01 to 0.99. In any embodiment of the graft copolymers disclosed herein, said second graft density may be selected from the range of 0.05 to 0.75. In any embodiment of the graft copolymers disclosed herein, said second graft density may be selected from the range of 0.05 to 0.32, 0.34 to 0.49, 0.51 to 0.65, or 0.68 to 0.75.

In any embodiment of the graft copolymers disclosed herein, said second graft distribution may be an alternating graft distribution when r^(b) ₁ is less than 1 and r^(b) ₂ is less than 1; said second graft distribution may be a blocky graft distribution when r^(b) ₁ is greater than 1 and r^(b) ₂ is greater than 1; said second graft distribution may be a random graft distribution when r^(b) ₁ is substantially equal to 1 and r^(b) ₂ is substantially equal to 1; and said second graft distribution may be a gradient graft distribution when r^(b) ₁ is less than 1 and r^(b) ₂ is greater than 1; where: r^(b) ₁ is a reactivity ratio of said second macromonomer; and r^(b) ₂ is a reactivity ratio of said second diluent group (or of said second reactive diluent).

In any embodiment of the graft copolymers disclosed herein, said second graft distribution may be an alternating graft distribution when r^(b) ₁ is substantially less than 1 and r^(b) ₂ is substantially less than 1; said second graft distribution may be a blocky graft distribution when r^(b) ₁ is substantially greater than 1 and r^(b) ₂ is substantially greater than 1; said second graft distribution may be a random graft distribution when r^(b) ₁ is substantially equal to 1 and r^(b) ₂ is substantially equal to 1; and said second graft distribution may be a gradient graft distribution when r^(b) ₁ is substantially less than 1 and r^(b) ₂ is substantially greater than 1; where: r^(b) ₁ is a reactivity ratio of said second macromonomer; and r^(b) ₂ is a reactivity ratio of said second diluent group (or of said second reactive diluent).

In any embodiment of the graft copolymers disclosed herein, said second graft distribution may be an alternating graft distribution when r^(b) ₁ is substantially less than 1 and r^(b) ₂ is substantially less than 1; said second graft distribution may be a blocky graft distribution when r^(b) ₁ is substantially greater than 1 and r^(b) ₂ is substantially greater than 1; said second graft distribution may be a random graft distribution when r^(b) ₁ is equal to 1 and r^(b) ₂ is equal to 1; and said second graft distribution may be a gradient graft distribution when r^(b) ₁ is substantially less than 1 and r^(b) ₂ is substantially greater than 1; where: r^(b) ₁ is a reactivity ratio of said second macromonomer; and r^(b) ₂ is a reactivity ratio of said second diluent group.

In any embodiment of the graft copolymers disclosed herein, said step of copolymerizing said second macromonomer may be performed in the presence of a catalyst. In any embodiment of the graft copolymers disclosed herein, the second polymer block may have a preselected second degree of polymerization, said second degree of polymerization being proportional to or equal to ([M^(b) ₁]₀+[M^(b) ₂]₀)/[Cat]₀; where: [Cat]₀ is initial concentration of said catalyst.

Additionally, graft copolymers of the present invention may have a low mass dispersity (low polydispersity index), which presents a number of benefits for applications in which the graft copolymers are used. In any embodiment of the graft copolymers disclosed herein, a polydispersity index of said graft copolymer is selected from the range of 1.00 to 1.30. In any embodiment of the graft copolymers disclosed herein, a polydispersity index of said graft copolymer is selected from the range of 1.00 to 1.20. In any embodiment of the graft copolymers disclosed herein, a polydispersity index of said graft copolymer is selected from the range of 1.00 to 1.10.

Some graft copolymers of the present invention have three or more polymer blocks, wherein a wide range of polymer block properties and arrangements are obtainable.

In any embodiment of the graft copolymers disclosed herein, the graft copolymer may be defined by the formula Q¹-[G¹]_(g)-[W¹]_(i)-[H¹]_(h)-Q², Q³-[W¹]_(i)-[G¹]_(g)-[H¹]_(h)-Q², or Q¹-[G¹]_(g)-[H¹]_(h)-[W¹]_(i)-Q³, where: G¹ is said first polymer block having the formula (FX20a), (FX20b), (FX20c), or (FX20d):

[(A′)_(m)-(B′)_(n)]  (FX20a);

[(B′)_(n)-(A′)_(m)]  (FX20b);

[(A′)_(m)-(B′)_(n)-(A′)_(x)]  (FX20d);

[(B′)_(n)-(A′)_(m)-(B′)_(y)]   (FX20d);

H¹ is said second polymer block having the formula (FX30a), (FX30b), (FX30c), or (FX30d):

[(A″)_(q)-(B″)_(s)]  (FX30a);

[(B″)_(s)-(A″)_(q)]  (FX30b);

[(A″)_(q)-(B″)_(s)-(A″)_(u)]  (FX30c);

[(B″)_(s)-(A″)_(q)-(B″)_(v)]   (FX30d);

A′ is said first repeating unit; B′ is a first diluent group; A″ is said second repeating unit; B″ is a second diluent group; Q¹ is a first polymer block terminating group; Q² is a second polymer block terminating group; g is a degree of polymerization of said first polymer block, and g is an integer selected from the range of 10 to 1000; h is a degree of polymerization of said second polymer block, and h is an integer selected from the range of 10 to 1000; each of m and q is independently an integer selected from the range of 10 to 999; each of n and s is independently an integer selected from the range of 1 to 990; each of x and y is independently an integer equal to (g−m−n); and each of u and v is independently an integer equal to (h−q−s); W¹ is a third polymer block; Q³ is a third polymer block terminating group; and i is a degree of polymerization of said third polymer block, and i an integer selected from the range of 10 to 1000; wherein the formulas (FX20a), (FX20b), (FX20c), and (FX20d) indicate amounts of A‘ and B’ which can have any distribution within G¹, and wherein the formulas (FX30a), (FX30b), (FX30c), and (FX30d) indicate amounts of A″ and B″ which can have any distribution within H¹.

In any embodiment of the graft copolymers disclosed herein, the graft copolymer may be defined by the formula Q¹-[G¹]_(g)-[W¹]_(i)-[W²]_(j)-[H¹]_(h)-Q², Q¹-[G¹]_(g)-[W²]_(j)-[W¹]_(i)-[H¹]_(h)-Q², Q³-[W¹]_(i)-[W²]1-[G¹]_(g)-[H¹]_(h)-Q², Q⁴-[W²]_(j)-[W²]_(i)-[G¹]_(g)-[H¹]_(h)-Q², Q¹-[G¹]_(g)-[H¹]_(h)-[W¹]_(i)-[W²]_(j)-Q⁴, or 01-[G¹]_(g)-[H¹]_(h)-[W¹]_(i)-[W¹]_(i)-Q³:

G¹ is said first polymer block having the formula (FX20a), (FX20b), (FX20c), or (FX20d):

[(A′)_(m)-(B′)_(n)]  (FX20a);

[(B′)_(n)-(A′)_(m)]  (FX20b);

[(A′)_(m)-(B′)_(n)-(A′)_(x)]  (FX20d);

[(B′)_(n)-(A′)_(m)-(B′)_(y)]   (FX20d);

H¹ is said second polymer block having the formula (FX30a), (FX30b), (FX30c), or (FX30d):

[(A″)_(q)-(B″)_(s)]  (FX30a);

[(B″)_(s)-(A″)_(q)]  (FX30b);

[(A″)_(q)-(B″)_(s)-(A″)_(u)]  (FX30c);

[(B″)_(s)-(A″)_(q)-(B″)_(v)]   (FX30d);

A′ is said first repeating unit; B′ is a first diluent group; A″ is said second repeating unit; B″ is a second diluent group; Q¹ is a first polymer block terminating group; Q² is a second polymer block terminating group; g is a degree of polymerization of said first polymer block, and g is an integer selected from the range of 10 to 1000; h is a degree of polymerization of said second polymer block, and h is an integer selected from the range of 10 to 1000; each of m and q is independently an integer selected from the range of 10 to 999; each of n and s is independently an integer selected from the range of 1 to 990; each of x and y is independently an integer equal to (g−m−n); each of u and v is independently an integer equal to (h−q−s); W¹ is a third polymer block; Q³ is a third polymer block terminating group; i is a degree of polymerization of said third polymer block, and i an integer selected from the range of 10 to 1000; W² is a fourth polymer block; Q⁴ is a third polymer block terminating group; and j is a degree of polymerization of said third polymer block, and j an integer selected from the range of 10 to 1000; wherein the formulas (FX20a), (FX20b), (FX20c), and (FX20d) indicate amounts of A‘and B’ which can have any distribution within G¹, and wherein the formulas (FX30a), (FX30b), (FX30c), and (FX30d) indicate amounts of A″ and B″ which can have any distribution within H¹.

Also provided herein are functional materials having graft copolymers such as those also provided herein. Functional materials provided herein include self-assembled polymer structures. The structure, chemistry, and other properties of the self-assembly of these structures disclosed herein may be highly tunable due to the highly versatile and tunable properties of the constituent graft copolymers. These self-assembled polymer structures have a broad set of applications, which include known and yet unknown potential applications. Exemplary applications include, but are not limited to, photonic materials, scaffolds for controlling nanoadditive distribution or orientation, scaffolds for growth of biological materials, and structures with gradient mechanical properties.

In an aspect, a self-assembled polymer structure comprises a plurality of graft block copolymers each independently being a graft copolymer of any embodiment of the graft copolymers disclosed herein.

In an aspect, a self-assembled polymer structure comprises a plurality of graft block copolymers each being identical to the others and being a graft copolymer of any embodiment of the graft copolymers disclosed herein.

In any embodiment of the self-assembled polymer structures disclosed herein, said self-assembled polymer structure may be a lamellar structure, a matrix-sphere structure, a matrix-cylinder structure, or a matrix-gyroid structure. In any embodiment of the self-assembled polymer structures disclosed herein, said polymer structure may be a lamellar structure and has a periodicity selected from the range of 20 nm to 400 nm. In any embodiment of the self-assembled polymer structures disclosed herein, said polymer structure may be a lamellar structure and has a periodicity selected from the range of 25 nm to 100 nm. In any embodiment of the self-assembled polymer structures disclosed herein, said polymer structure may be a lamellar structure and has a total thickness in a transverse direction selected from the range of 40 nm to 1400 nm.

In any embodiment of the self-assembled polymer structures disclosed herein, the self-assembled polymer structure may be at least partially configured as a photonic crystal. In any embodiment of the self-assembled polymer structures disclosed herein, said photonic crystal is configured to reflect visible light. In any embodiment of the self-assembled polymer structures disclosed herein, the self-assembled polymer structure may be configured as a transmissive surface coating, configured to substantially transmit at least a portion of visible light, a partially reflective surface coating, configured to substantially reflect at least a portion of visible light, a photonic crystal, a solid polymer electrolyte, a scaffold, a gradient mechanical property structure, or a combination thereof.

In any embodiment of the self-assembled polymer structures disclosed herein, one or more polymer blocks of one or more graft copolymers of said plurality of graft block copolymers may be a linear-type block copolymer. In any embodiment of the self-assembled polymer structures disclosed herein, one or more polymer blocks of one or more graft copolymers of said plurality of graft block copolymers may be a comb-type block copolymer. In any embodiment of the self-assembled polymer structures disclosed herein, one or more polymer blocks of one or more graft copolymers of said plurality of graft block copolymers may be a bottlebrush-type block copolymer.

In an aspect, a method for forming a self-assembled polymer structure comprises the steps of: (a) providing a plurality of graft block copolymers each independently being a graft copolymer of any embodiment of the graft copolymers disclosed herein; and (b) inducing self-assembly of said plurality of graft block copolymers. In any embodiment of the methods for forming a self-assembled polymer structure disclosed herein, said step of inducing may comprise pressure annealing under a contact pressure selected from the range of 100 kPa to 200 kPa. In any embodiment of the methods for forming a self-assembled polymer structure disclosed herein, said step of inducing may comprise pressure annealing under a contact pressure selected from the range of 100 kPa to 120 kPa. In any embodiment of the methods for forming a self-assembled polymer structure disclosed herein, said step of inducing may comprise temperature annealing at an annealing temperature selected from the range of 50° C. to 150° C. In any embodiment of the methods for forming a self-assembled polymer structure disclosed herein, said step of inducing may comprise temperature annealing at an annealing temperature selected from the range of 30° C. to 50° C.

In any embodiment of the methods for forming a self-assembled polymer structure disclosed herein, said self-assembled polymer structure may be a lamellar structure, a matrix-sphere structure, a matrix-cylinder structure, or a matrix-gyroid structure.

In an aspect, a self-assembled polymer structure comprises: a plurality of graft block copolymers, each graft block copolymer independently comprising: a first polymer block comprising at least 10 first repeating units; each of said first repeating units comprising a first polymer backbone group and directly or indirectly covalently linked to a first polymer side chain group; wherein said first polymer block further comprises a first diluent group incorporated into a first backbone of said first polymer block and provided in an amount such that said first polymer block is characterized by a preselected first graft density or a preselected first graft distribution of said first repeating units; and a second polymer block comprising at least 10 second repeating units; each of said second repeating unit comprising a second polymer backbone group directly or indirectly covalently linked to a second polymer side chain group; wherein said second polymer block has a second backbone directly or indirectly covalently linked to said first backbone of said first polymer block; and wherein said second polymer block further comprises a second diluent group incorporated into said second backbone of said second polymer block and provided in an amount such that said second polymer block is characterized by a preselected second graft density or a preselected second distribution of said second repeating units; wherein said first polymer bock and said second polymer block are directly or indirectly linked to each other. In an embodiment of the self-assembled polymer structure of this aspect: (i) said preselected first graft density and/or or said preselected second graft density is any value selected from the range of 0.05 to 0.75; and/or (ii) said first polymer block is characterized by a preselected first graft density and a preselected first graft distribution of said first repeating units; and/or (iii) said second polymer block is characterized by a preselected second graft density and a preselected second distribution of said second repeating units; and/or (iv) said second polymer side chain group is different from said first polymer side chain group; and/or (v) said second polymer backbone group is different from said first polymer backbone group; and/or (vi) said preselected first graft density and/or said preselected second graft density is selected from the range of 0.01 to 0.99; and/or (vii) each graft block copolymer of the self-assembled polymer structure comprises one or more additional polymer blocks directly or indirectly covalently linked to said first backbone of said first polymer block or said second backbone of said second polymer block; and/or (viii) a polydispersity index of said each graft block copolymer is selected from the range of 1.00 to 1.30, 1.00 to 1.20, or 1.00 to 1.10.

In an aspect, a method of synthesizing a graft copolymer comprises a step of: copolymerizing a first macromonomer and a first reactive diluent; wherein said first macromonomer comprises a first backbone precursor directly or indirectly covalently linked to a first polymer side chain group; wherein said reactive diluent is provided in the presence of the first macromonomer at an amount selected so as to result in formation said graft copolymer having a first backbone incorporating said diluent and said first macromonomer in a first polymer block characterized by a preselected first graft density or a preselected first graft distribution of said first macromonomer. In an embodiment of the method of this aspect: (i) said preselected first graft density and/or or said preselected second graft density is any value selected from the range of 0.05 to 0.75; and/or (ii) the composition and amount of said diluent is selected to provide both a first preselected first graft density and a first preselected first graft distribution; and/or (iii) the method further comprises one or more additional copolymerization steps, so as to result in said graft copolymer having one or more additional polymer blocks directly or indirectly covalently linked to said first backbone of said first polymer block; and/or (iv) said preselected first graft density is selected from the range of 0.01 to 0.99, or is selected from the range of 0.05 to 0.32, 0.34 to 0.49, 0.51 to 0.65, or 0.68 to 0.75; and/or (v) a polydispersity index of said graft copolymer is selected from the range of 1.00 to 1.30, 1.00 to 1.20, or 1.00 to 1.10.

In an aspect, a method of synthesizing a graft copolymer comprises a step of: copolymerizing a first macromonomer and a first reactive diluent; wherein said first macromonomer comprises a first backbone precursor directly or indirectly covalently linked to a first polymer side chain group; wherein said reactive diluent is provided in the presence of the first macromonomer at an amount selected so as to result in formation said graft copolymer having a first backbone incorporating said diluent and said first macromonomer in a first polymer block characterized by a preselected first graft density or a preselected first graft distribution of said first macromonomer. In an embodiment of the method of this aspect: (i) said preselected first graft density and/or or said preselected second graft density is any value selected from the range of 0.05 to 0.75; and/or (ii) the composition and amount of said diluent is selected to provide both a first preselected first graft density and a first preselected first graft distribution; and/or (iii) the method further comprises a step of copolymerizing a second macromonomer and a second reactive diluent, wherein said second macromonomer comprises a second backbone precursor directly or indirectly covalently linked to a second polymer side chain group, wherein said second reactive diluent is provided in the presence of the second macromonomer at an amount selected so as to result in formation said graft copolymer having a second backbone incorporating said second reactive diluent and said second macromonomer in a second polymer block characterized by a preselected second graft density or a preselected second graft distribution of said second macromonomer, and wherein said first polymer block and said second polymer block are directly or indirectly covalently linked along said backbone; wherein said second polymer side chain group may be different from said first polymer side chain group; wherein said second polymer backbone group may be different from said first polymer backbone group; and wherein said second polymer block may be characterized by a preselected second graft density and a preselected second distribution of said second repeating units; and/or (iv) said preselected first graft density and/or said preselected second graft density is selected from the range of 0.01 to 0.99, or is selected from the range of 0.05 to 0.32, 0.34 to 0.49, 0.51 to 0.65, or 0.68 to 0.75; and/or (v) a polydispersity index of said graft copolymer is selected from the range of 1.00 to 1.30, 1.00 to 1.20, or 1.00 to 1.10.

In an aspect, a graft copolymer comprises a first polymer block comprising at least 10 first repeating units; each of said first repeating units comprising a first polymer backbone group and directly or indirectly covalently linked to a first polymer side chain group; wherein said first polymer block further comprises a first diluent group incorporated into a first backbone of said first polymer block and provided in an amount such that said first polymer block is characterized by a preselected first graft density or a preselected first graft distribution of said first repeating units. In an embodiment of a graft copolymer of this aspect: (i) said preselected first graft density and/or or said preselected second graft density is any value selected from the range of 0.05 to 0.75; and/or (ii) said first polymer block is characterized by a preselected first graft density and a preselected first graft distribution of said first repeating units; and/or (iii) a polydispersity index of said graft copolymer is selected from the range of 1.00 to 1.30, 1.00 to 1.20, or 1.00 to 1.10; and/or (iv) said preselected first graft density and/or said preselected second graft density is selected from the range of 0.01 to 0.99, or is selected from the range of 0.05 to 0.32, 0.34 to 0.49, 0.51 to 0.65, or 0.68 to 0.75; and/or (v) the graft copolymer further comprises one or more additional polymer blocks directly or indirectly covalently linked to said first backbone of said first polymer block.

In an aspect, a graft copolymer comprises a first polymer block comprising at least 10 first repeating units; each of said first repeating units comprising a first polymer backbone group and directly or indirectly covalently linked to a first polymer side chain group; wherein said first polymer block further comprises a first diluent group incorporated into a first backbone of said first polymer block and provided in an amount such that said first polymer block is characterized by a preselected first graft density or a preselected first graft distribution of said first repeating units. In an embodiment of a graft copolymer of this aspect: (i) said preselected first graft density and/or or said preselected second graft density is any value selected from the range of 0.05 to 0.75; and/or (ii) said first polymer block is characterized by a preselected first graft density and a preselected first graft distribution of said first repeating units; and/or (iii) a polydispersity index of said graft copolymer is selected from the range of 1.00 to 1.30, 1.00 to 1.20, or 1.00 to 1.10; and/or (iv) said preselected first graft density and/or said preselected second graft density is selected from the range of 0.01 to 0.99, or is selected from the range of 0.05 to 0.32, 0.34 to 0.49, 0.51 to 0.65, or 0.68 to 0.75; and/or (v) the graft copolymer further comprises said graft copolymer may be a graft block copolymer; said graft block copolymer further comprising: a second polymer block comprising at least 10 second repeating units; each of said second repeating unit comprising a second polymer backbone group directly or indirectly covalently linked to a second polymer side chain group; wherein said second polymer block has a second backbone directly or indirectly covalently linked to said first backbone of said first polymer block; and wherein said second polymer block further comprises a second diluent group incorporated into said second backbone of said second polymer block and provided in an amount such that said second polymer block is characterized by a preselected second graft density or a preselected second distribution of said second repeating units; wherein said second polymer side chain group may be different from said first polymer side chain group; wherein said second polymer backbone group may be different from said first polymer backbone group; and wherein said second polymer block may be characterized by a preselected second graft density and a preselected second distribution of said second repeating units.

Without wishing to be bound by any particular theory, there may be discussion herein of beliefs or understandings of underlying principles relating to the devices and methods disclosed herein. It is recognized that regardless of the ultimate correctness of any mechanistic explanation or hypothesis, an embodiment of the invention can nonetheless be operative and useful.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1. An illustrative summary of exemplary methods and graft copolymers having preselected graft density and/or graft distribution.

FIG. 2. An illustration of an exemplary method and exemplary resulting graft copolymers in accordance with the present invention, where grafting density and side chain distribution may be controlled and preselected.

FIG. 3. Left: Structures of macromonomers (PS, PLA, PDMS) and diluents (DME, DEE, DBE). Right: Plots of In([M]₀/[M]_(t)) versus time, showing first-order kinetics for the homopolymerization of norbornene monomers (0.05 M) catalyzed by G3 (0.5 mM) in CH₂Cl₂ at 298 K (orange stars: PDMS, inverted red triangles: DME, green squares: PLA, brown diamonds: DEE, purple triangles: DBE, blue circles=PS). The numbers in parentheses represent the values of k_(obs) (10⁻³ s⁻¹) under the reaction conditions.

FIG. 4. Terminal model describing the copolymerization of M₁ and M₂, including exemplary conditions for exemplary graft distributions of graft copolymers.

FIG. 5. (Top) Illustration of a process of copolymerization of PS (0.05 M) and DME (0.05 M) catalyzed by G3 (0.5 mM) in CH₂Cl₂ at 298 K. FIG. 5, panel A: Normalized differential refractive index (dRI) trace from size-exclusion chromatography (SEC). The different traces correspond to aliquots extracted at different times. At elution times (x-axis) of less than 16 minutes, the right-most to left-most data curves correspond to aliquots taken at 1, 3, 5, 7, 9, and 12 minutes, respectively. At elution times (x-axis) of greater than 16 minutes, the top-most to bottom data curves correspond to aliquots taken at 1, 3, 5, 7, 9, and 12 minutes, respectively. FIG. 5, panel B: Plots of In([M]₀/[M]_(t)) versus time as monitored by ¹H NMR spectroscopy (filled blue circles=PS, filled red triangles=DME). Unfilled blue circles (PS), unfilled red triangles (DME), and the solid lines, plotted for comparison, are obtained from homopolymerization reactions under the same conditions.

FIGS. 6A-6D. Non-linear least-square curve fitting for the copolymerization of (FIGS. 6A-6B) PS (0.05 M) and DME (0.05 M) and (FIGS. 6C-6D) PS (0.05 M) DME (0.10 M) in CH₂Cl₂ at 298 K. [G3]₀=0.5 mM. Calculated fits (solid lines) show close agreement with the measured values (points). In FIGS. 6B and 6D, the dashed lines, included for comparison, indicate ideal random copolymerization (r₁=r₂=1).

FIG. 7. A chemical structure of a reactive propagating species PS*.

FIGS. 8A-8L. Non-linear least-square curve fitting for the copolymerization of various macromonomer/diluent pairs: (FIGS. 8A-8B) PS/DEE, (FIGS. 8C-8D) PS/DBE, (FIGS. 8E-8F) PLA/DME, (FIGS. 8G-8H) PLA/DBE, (FIGS. 8I-8J) PDMS/DME, and (FIGS. 8K-8L) PDMS/DBE (0.055 M). Reaction conditions: [M]₀=0.05 M unless otherwise indicated, [G3]₀=0.5 mM, solvent=CH₂Cl₂, temperature=298 K.

FIGS. 9A-9D. Simulated copolymer compositions for (FIG. 9A) PS:DME=1:1; (FIG. 9B) PLA:DME=1:1; (FIG. 9C) PDMS:DME=1:1; (FIG. 9D) PDMS:DBE=1:1. Insets show the schematic illustrations of the corresponding polymers.

FIG. 10. SEC traces of (PLA^(x)-ran-DME^(1-x))_(n) where x=grafting density (1.0, 0.75, 0.5, 0.25), n=targeted total backbone degree of polymerization (red: 167, orange: 133, green: 100, teal: 67, purple: 33), and “ran” indicates a random distribution of PLA polymer side chains, or branches. The data curves from left-to-right correspond to n of 167, 133, 100, 67, and 33, respectively. Schematics on the right show the schematic illustrations of corresponding copolymers.

FIG. 11. ¹H NMR spectrum of PS in CDCl₃.

FIG. 12. ¹H NMR spectrum of PLA in CDCl₃.

FIG. 13. ¹H NMR spectrum of PDMS in CDCl₃.

FIG. 14. ¹H NMR spectrum of DME in CDCl₃.

FIG. 15. ¹H NMR spectrum of DEE in CDCl₃.

FIG. 16. ¹H NMR spectrum of DBE in CDCl₃.

FIG. 17. SEC traces of PS (D=1.04), PLA (D=1.05), and PDMS (⊗=1.03) macromonomers. Note that the retention time does not reflect the actual molar masses of the macromonomers due to different interactions between the macromonomers and the mobile phase (THF). The molar masses of the macromonomers are determined by ¹H NMR spectroscopy. The data curves from left-to-right correspond to PLA, PS, and PDMS, respectively.

FIG. 18. Selected ¹H NMR spectra (solvent: CDCl₃) obtained from the copolymerization reaction of PS with DBE (1:1) as an example, showing the depletion of the olefinic resonances which may be integrated against the aromatic polystyrene resonances.

FIGS. 19A-19B. Non-linear least-square curve fitting for the copolymerization of PS (0.075 M) and DBE (0.025 M) in CH₂Cl₂ at 298 K. [G3]₀=0.5 mM: FIG. 19A is a plot of [M]_(t) vs. time and FIG. 19B is a plot of total conversion vs. monomer conversion. Calculated fits (solid lines) show close agreement with the measured values (points). In FIG. 19B, the dashed lines indicate random copolymerization (r₁=r₂=1).

FIG. 20. Differential scanning calorimetry (DSC) data for PS₁₀₀, DBE₁₀₀, and two copolymers thereof: (PS₁₀₀-b-DBE₁₀₀), a block copolymer with one fully grafted block and one ungrafted block, synthesized by sequential addition of PS and DBE; and (PS^(0.5)-ran-DBE^(0.5))₂₀₀, a random bottlebrush copolymer with 50% grafting density, synthesized by copolymerizing PS and DBE in a 1:1 feed ratio as discussed in the text. The data are collected on the second heating cycle using a 10° C./min ramp rate, and glass transition temperatures (T_(g), open circles) are identified from the corresponding derivative curves. Both copolymers exhibit a single T_(g) between the T_(g)s of the pure components, indicating successful incorporation of both PS and DBE. The T_(g) of PS₁₀₀-b-DBE₁₀₀ (which has a guaranteed blocky sequence due to sequential addition and complete consumption of each block) differs from the T_(g) of (PS^(0.5)-ran-DBE^(0.5))₂₀₀ in terms of both position and shape, suggesting that (PS^(0.5)-ran-DBE^(0.5))₂₀₀ is at least not blocky and instead likely random.

FIG. 21. An illustrative summary of exemplary reactive diluent and macromonomer species in accordance with the present invention.

FIG. 22A-22B. Grafting-through ROMP of a small-molecule diluent (white) and a macromonomer (black). Since the side chains (red, squiggly lines) are connected to certain backbone units, control over the backbone sequence directly determines the side chain distribution: (FIG. 22A) uniform, (FIG. 22B) gradient, etc. The anticipated average cross-sectional radius of gyration (R_(c)) is indicated. For ease of visualization, chains are illustrated in the limit of fully extended backbones.

FIG. 23. Monomer design for ring-opening metathesis copolymerization, demonstrating exemplary reactive diluent species in accordance with the present invention.

FIG. 24. Homopolymerization rate constants (k_(homo)) for substituted endo,exo-norbornenyl diester monomers (left to right: 1a-j). k_(homo) decreases with increasing steric bulk (R=Me to ^(t)Bu, 1a-f). k_(homo) does not change significantly with electronic changes via fluorination (1g) or para-substitution of a phenyl ring (1 h-j).

FIG. 25A. Homopolymerization rate constants (k_(homo)) for monomers with exo,exo-diester (xx, green), endo,exo-diester (dx, red), and endo,endo-diester (dd, yellow) anchor groups. Comparison of k_(homo) for monomers with R=Me, Et, ^(n)Pr, and ^(n)Bu supports the steric influences of stereochemistry and substituent size. Top most points correspond to exo,exo-diester (xx, green), middle points correspond to endo,exo-diester (dx, red), and bottom points correspond to endo,endo-diester (dd, yellow). FIG. 25B. k_(homo) for Me- and ^(n)Bu-substituted monomers with each of the five anchor groups; endo-imide (d-l, blue) and exo-imide (x-l, purple).

FIG. 26. Plot of k_(homo) values for all monomers studied herein. The monomers are sorted according to their anchor groups: left to right: endo,exo-diester (red, 1a-j), endo,endo-diester (yellow, 2a-d), exo,exo-diester (green, 3a-d), endo-imide (blue, 4a-c), and exo-imide (purple, 5a-c and macromonomers). k_(homo) values for methyl-substituted monomers are provided for comparison.

FIG. 27A. Proposed dissociative ROMP pathway for a G3 catalyst. FIG. 27B. DFT-calculated free energy diagram corresponding to one ROMP cycle for endo- (2a, blue) and exo-substituted (3a, red) norbornenyl monomers. The following intermediates are calculated: (a) six-membered Ru—O chelate, (b) 14-electron vacant species, (c) olefin adduct, and (d) metallacyclobutane.

FIG. 28. Propagation reactions for the copolymerization of a discrete diluent (M₂, dx-DE shown for example) and a macromonomer (M₁) according to a terminal model. M₂* and M₁* are the corresponding propagating alkylidene species. (A) Diluent self-propagation (k₂₂), (B) cross-propagation (k₂₁), (C) macromonomer self-propagation (k₁₁), (D) cross-propagation (k₁₂).

FIG. 29A. Copolymerization scheme: the same macromonomer (PLA, M₁) is copolymerized with 13 different reactive diluents (M₂). The feed ratio (x/y=1) and total backbone length (x+y=200) are fixed. FIG. 29B. M₂ (exemplary reactive diluent species in accordance with the present invention) arranged in order of increasing k₂₂.

FIG. 29C. PLA/diluent copolymerization data. Left axis, black: self-propagation rate constants (k₂₂: filled circles, k₁₁: open circles). Right axis, red: reactivity ratios (r₂: solid line, r₁: dotted line).

FIGS. 30A-30C. Simulated sequences and (inset) graft polymer architectures for the copolymerization of PLA with different diluents: (FIG. 30A) 4a, (FIG. 30B) 1a, or (FIG. 30C) 5a. For ease of visualization, the simulated structures show fully extended side chains and backbones.

FIG. 31. Data for the copolymerization of M₁=PDMS (left) or PS (right) with different diluents. Left axis, black: self-propagation rate constants (k₂₂: filled circles, k₁₁: open circles). Right axis, red: reactivity ratios (r₂: solid line, r₁: dotted line).

FIG. 32. Reactivity ratio map. The copolymerization kinetics studied for PLA, PDMS, and PS are interpreted in terms of the quotient r₁/r₂, plotted on the x-axis. For ease of visualization, the simulated structures show fully extended side chains and backbones.

FIG. 33A. Illustrations of three AB graft diblock polymers, differing in the side chain distribution: uniform (BP-1), gradient (BP-2), and inverse-gradient (BP-3). The horizontal dotted line indicates the junction between blocks. FIG. 33B. SAXS patterns corresponding to the annealed block polymers: (i) BP-1, (ii) BP-2, (iii) BP-3. The white “x” indicates the first-order diffraction peak, q*.

FIG. 34A-34C. Schematic illustration of the relationships between chain dimensions and the lamellar period. FIG. 34A. d_(A)≈3d_(B) is expected if the backbones are fully stretched (since N_(bb,A)=3N_(bb,B)), but it is consistent with SAXS data. FIG. 34B. Instead, d_(A)≈d_(B) is observed. This requires bending of the A block backbone. FIG. 34C. Illustration of BP-3 and revised chain conformations.

FIG. 35. A plots of scaling exponent (α) vs. graft density (z) and of predicted total backbone degree of polymerization (Nbb) vs. graft density (z) for exemplary copolymers, or polymer structures therewith, of the present invention.

FIG. 36. Illustrations of exemplary copolymers (left: linear; right: bottlebrush-type graft block copolymer) and corresponding lamellar self-assembled structures therewith.

FIG. 37. Synthesis of (PLA^(z)-r-DME^(1-z))_(n)-b-(PS^(z)-r-DBE^(1-z))_(n) block polymers (System I) featuring variable backbone degrees of polymerization (N_(bb)=2n=44-363) and grafting densities (z=1.00, 0.75, 0.50, 0.35, 0.25, 0.20, 0.15, 0.05, 0).

FIG. 38. Top: Scheme of System I, consisting of block copolymer (PLA^(z)-r-DME^(1-z))_(n)-b-(PS^(z)-r-DBE^(1-z))_(n) with variable total backbone degrees of polymerization (N_(bb)=2n) and grafting densities (z), where “r” represent a random graft distribution (e.g., within respective polymer block) and “b” represent a blocky distribution of the different polymer blocks of the overall graft block copolymer. FIG. 38, panel A: Stacked 1 D azimuthally averaged SAXS profiles for z=1, indicating well-ordered lamellar morphologies. FIG. 38, panel B: Experimental data for the lamellar period (d*) and N_(bb) (circles), as well as calculated power-law fits (d*˜N_(bb) ^(α), lines). The data curves top-to-bottom correspond to graft densities of z=1.00 to z=0.00, respectively (see legend). FIG. 38, panel C: Plot of the scaling exponents (α) as a function of z. A transition occurs around z=0.2 (dotted line). The data curves left-to-right correspond to graft densities of z=0.00 to z=1.00, respectively.

FIG. 39. Scanning electron micrographs of graft block polymers with (FIG. 39, panel A) z=1.00, (PLA)₁₀₀-b-(PS)₁₀₀; (FIG. 39, panel B) z=0.75, (PLA^(0.75)-r-DME^(0.25))₁₁₀-b-(PS^(0.75)-r-DBE^(0.25))₁₁₀; (FIG. 39, panel C) z=0.50, (PLA^(0.5)-r-DME^(0.5))₁₀₄-b-(PS^(0.5)-r-DBE^(0.5))₁₀₄; and (FIG. 39, panel D) z=0.25, (PLA^(0.25)-r-DME^(0.75))₁₁₂-b-(PS^(0.25)-r-DBE^(0.75))₁₁₂.

FIG. 40. (PLA^(z)-r-DBE^(1-z))_(n)-b-(PS^(z)-r-DBE^(1-z))_(n) of variable backbone degrees of polymerization (N_(bb)=2n=82-533) and grafting densities (z=0.75, 0.50, 0.35, 0.25, 0.15, 0.12, 0.06, and 0.05).

FIG. 41. Top: Scheme of System II, consisting of block polymer (PLA^(z)-r-DBE^(1-z))_(n)-b-(PS^(z)-r-DBE^(1-z))_(n) with variable total backbone degrees of polymerization (N_(bb)=2n) and grafting densities (z). FIG. 41, panel A. Stacked 1 D azimuthally averaged SAXS profiles for z=0.75, indicating well-ordered lamellar morphologies. FIG. 41, panel B. Experimental data for the lamellar period (d*) and N_(bb) (circles), as well as calculated power-law fits (d*˜N_(bb) ^(α), lines). The data curves top-to-bottom correspond to graft densities of z=1.00 to z=0.05, respectively (see legend). FIG. 41, panel C. Plot of the scaling exponents (a) as a function of z. A transition occurs around z=0.2 (dotted line). The data curves left-to-right correspond to graft densities of z=0.05 to z=1.00, respectively. Note that in FIG. 41, panel B, and FIG. 41, panel C, unfilled circles indicate data for System I (z=1.00), in which the side chain molecular weights are slightly higher.

FIG. 42. Plots of predicted N_(bb) required to access d*=200 nm as a function of grafting density (z) for (FIG. 42, panel A) System I and (FIG. 42, panel B) System II.

FIG. 43A-43B. Analysis of scaling trends with grafting density (z) for (FIG. 43A) System I and (FIG. 43B) System II. (top) Experimentally determined values and lines of best fit for the scaling exponent (a) versus z. The lines intersect at a critical z_(c), associated with a transition in the backbone stiffness. In FIG. 43B, the unfilled circle (z=1.00) indicates data for System I. (bottom) Calculated root-mean-square end-to-end distances, normalized by the backbone statistical segment length (√{square root over (

R²

)}/a₀), fixing N_(bb)=100.

FIGS. 44A-44J. NMR spectra corresponding to certain structures or materials discussed in Examples 2A and 2B (e.g., “1a”, “1b”, and “1c”, some of which are illustrated in FIG. 23 and FIG. 29B, for example). FIG. 44A. ¹H NMR spectrum of 1a in CDCl₃; FIG. 44B. ¹H NMR spectrum of 1b in CDCl₃; FIG. 44C. ¹H NMR spectrum of 1c in CDCl₃; FIG. 44D. ¹H NMR spectrum of 1d in CDCl₃; FIG. 44E. ¹H (top) and ¹³C (bottom) NMR spectra of 1e in CDCl₃; FIG. 44F. ¹H (top) and ¹³C (bottom) NMR spectra of 1f in CDCl₃; FIG. 44G. ¹H (top), ¹³C (middle), and ¹⁹F (bottom) NMR spectra of 1g in CDCl₃; FIG. 44H. ¹H NMR spectrum of 1h in CDCl₃; FIG. 44I. ¹H (top), ¹³C (middle), and ¹⁹F (bottom) NMR spectra of 1i in CDCl₃; FIG. 44J. ¹H (top) and ¹³C (bottom) NMR spectra of 1j in CDCl₃.

FIGS. 45A-45D. NMR spectra corresponding to certain structures or materials discussed in Examples 2A and 2B (e.g., “2a”, “2b”, and “2c”, some of which are illustrated in FIG. 23 and FIG. 29B, for example). FIG. 45A. ¹H (top) and ¹³C (bottom) NMR spectra of 2a in CDCl₃; FIG. 45B. ¹H (top) and ¹³C (bottom) NMR spectra of 2b in CDCl₃; FIG. 45C. ¹H (top) and ¹³C (bottom) NMR spectra of 2c in CDCl₃; FIG. 45D. ¹H (top) and ¹³C (bottom) NMR spectra of 2d in CDCl₃.

FIGS. 46A-46D. NMR spectra corresponding to certain structures or materials discussed in Examples 2A and 2B (e.g., “3a”, “3b”, and “3c”, some of which are illustrated in FIG. 23 and FIG. 29B, for example). FIG. 46A. ¹H (top) and ¹³C (bottom) NMR spectra of 3a in CDCl₃; FIG. 46B. ¹H (top) and ¹³C (bottom) NMR spectra of 3b in CDCl₃; FIG. 46C. ¹H (top) and ¹³C (bottom) NMR spectra of 3c in CDCl₃; FIG. 46D. ¹H (top) and ¹³C (bottom) NMR spectra of 3d in CDCl₃.

FIGS. 47A-47C. NMR spectra corresponding to certain structures or materials discussed in Examples 2A and 2B (e.g., “4a”, “4b”, and “4c”, some of which are illustrated in FIG. 23 and FIG. 29B, for example). FIG. 47A. ¹H NMR spectrum of 4a in CDCl₃; FIG. 47B. ¹H (top) and ¹³C (bottom) NMR spectra of 4b in CDCl₃; FIG. 47C. ¹H (top) and ¹³C (bottom) NMR spectra of 4c in CDCl₃.

FIGS. 48A-48C. NMR spectra corresponding to certain structures or materials discussed in Examples 2A and 2B (e.g., “5a”, “5b”, and “5c”, some of which are illustrated in FIG. 23 and FIG. 29B, for example). FIG. 48A. ¹H NMR spectrum of 5a in CDCl₃; FIG. 48B. ¹H (top) and ¹³C (bottom) NMR spectra of 5b in CDCl₃; FIG. 48C. ¹H (top) and ¹³C (bottom) NMR spectra of 5c in CDCl₃.

FIGS. 49A-49B. Plots of In([M]₀/[M]_(t)) vs. time used to determine rate constants for certain materials corresponding to Examples 2A and 2B. Representative repeated runs to determine rate constants (k_(homo)) for (FIG. 49A) 1a, endo,exo-norbornenyl dimethylester; and (FIG. 49B) PLA, poly(D,L-lactide) macromonomer. k_(homo) is calculated from Eq. 1.

FIG. 50. Stacked ¹H NMR spectra obtained during the pyridine titration experiments, corresponding to Examples 2A and 2B. To an NMR tube containing a CD₂Cl₂ solution of the monopyridine complex (11.2 mM) was titrated with a CD₂Cl₂ solution containing both pyridine (1.47 M) and the monopyridine complex (11.2 mM). The concentration of the monopyridine complex remained constant during the titrations. The chemical shifts of the benzylidene ¹H resonance was monitored at 298 K and could be employed to fit the pyridine binding constant (K_(binding)=1/K_(eq,1)).

FIG. 51. ROMP of 5a (left) and 5b (right) in CH₂Cl₂ at 298 K showing the rate dependence on catalyst initial concentration [G3]₀ (maroon (big squares): [G3]₀=0.5 mM, blue (small squares): [G3]₀=0.05 mM, green (triangles): [G3]₀=0.025 mM). The slope corresponds to the k_(obs) (s⁻¹). These polymerization reactions have the same [5a]₀/[G3]₀ and [5b]₀/[G3]₀ ratio of 100. Time-lapse kinetic traces were obtained using our standard homopolymerization procedure. These data correspond to Examples 2A and 2B.

FIGS. 52A-52F. DFT-optimized structures of catalytically relevant ruthenium species, corresponding to the proposed dissociative ROMP pathway, which is illustrated in FIG. 52F and FIGS. 27A-27B. FIGS. 52A-52E correspond to structures of chemical species such as intermediate species of the ROMP pathway of FIG. 52F: (FIG. 52A) Six-membered Ru—O chelate, (FIG. 52B) 14-electron vacant species, (FIG. 52C) olefin adduct, (FIG. 52D) metallacyclobutane intermediate, and (FIG. 52E) monopyridine adduct. The labels “A”, “B”, “C”, “via D”, and “E” in FIG. 52F correspond to the chemical structures of FIGS. 52A, 52B, 52C, 52D, and 52E, respectively. These data correspond to Examples 2A and 2B.

FIG. 53. SEC traces for PLA and diluent copolymerizations at full conversion. These data correspond to Examples 2A and 2B.

FIG. 54. SEC traces for PDMS and diluent copolymerizations at full conversion. These data correspond to Examples 2A and 2B. The data curves from left-to-right correspond to M₂ of 3d, 3a, 4b, 1d, 1a, and 4a, respectively (M₁ is PDMS in each case).

FIG. 55. SEC traces for PS and diluent copolymerizations at full conversion. These data correspond to Examples 2A and 2B.

FIG. 56. (Top) Chemical structures of graft block polymers BP-1, BP-2, and BP-3. (Bottom) Schematic illustrations of the anticipated molecular “shapes,” drawn in the limit of fully extended backbones for ease of visualization. These data correspond to Examples 2A and 2B.

FIG. 57. SEC traces for graft block polymers BP-1, BP-2, and BP-3, indicating essentially identical molecular weights and dispersities. These data correspond to Examples 2A and 2B. The data curves from left-to-right correspond to BP-3, BP-2, and BP-1, respectively.

FIG. 58. ¹H NMR data for graft block polymers BP-1, BP-2, and BP-3, indicating essentially identical chemical compositions (f≈0.5). Illustrations of the corresponding polymer chain distributions and arrangements are shown on the left. These data correspond to Examples 2A and 2B.

FIG. 59. SEC traces; (top) System I, z=1.00, 1^(st) block; System I, z=1.00 (bottom). These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to A5 to A1, respectively.

FIG. 60. SEC traces; (top) System I, z=0.75, 1^(st) block; System I, z=0.75 (bottom). (“z” represents graft density.) These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to B4 to B1, respectively.

FIG. 61. SEC traces; (top) System I, z=0.50, 1^(st) block; System I, z=0.50 (bottom). These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to C4 to C1, respectively.

FIG. 62. SEC traces; (top) System I, z=0.35, 1^(st) block; System I, z=0.35 (bottom). These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to D6 to D1, respectively.

FIG. 63. SEC traces; (top) System I, z=0.25, 1^(st) block; System I, z=0.25 (bottom). These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to E7 to E1, respectively.

FIG. 64. SEC traces; (top) System I, z=0.20, 1^(st) block; System I, z=0.20 (bottom). These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to F7 to F1, respectively.

FIG. 65. SEC traces; (top) System I, z=0.15, 1^(st) block; System I, z=0.15 (bottom). These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to G6 to G1, respectively.

FIG. 66. SEC traces; (top) System I, z=0.05, 1^(st) block; System I, z=0.05 (bottom). These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to H6 to H1, respectively.

FIG. 67. SEC traces; (top) System I, z=0.00, 1^(st) block; System I, z=0.00 (bottom). These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to 16 to 11, respectively.

FIG. 68 SEC traces; (top) System II, z=0.75, 1^(st) block; System II, z=0.75 (bottom). These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to J6 to J1, respectively.

FIG. 69. SEC traces; (top) System II, z=0.50, 1^(st) block; System II, z=0.50 (bottom). These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to K6 to K1, respectively.

FIG. 70. SEC traces; (top) System II, z=0.35, 1^(st) block; System II, z=0.35 (bottom). These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to L6 to L1, respectively.

FIG. 71. SEC traces; (top) System II, z=0.25, 1^(st) block; System II, z=0.25 (bottom). These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to M₆ to M₁, respectively.

FIG. 72. SEC traces; (top) System II, z=0.15, 1^(st) block; System II, z=0.15 (bottom). These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to N6 to N1, respectively.

FIG. 73. SEC traces; (top) System II, z=0.12, 1^(st) block; System II, z=0.12 (bottom). These data correspond to Examples 3A and 3B. The data curves left-to-right correspond to 06 to 01, respectively.

FIG. 74. SEC traces; (top) System II, z=0.06, 1^(st) block; System II, z=0.06 (bottom). These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to P5 to P1, respectively.

FIG. 75. SEC traces; (top) System II, z=0.05, 1^(st) block; System II, z=0.05 (bottom). These data correspond to certain structures of Examples 3A and 3B. The data curves left-to-right correspond to Q4 to Q1, respectively.

FIGS. 76A-76B. Raw 2D SAXS data for z=0.05 graft polymers: (FIG. 76A) (PLA^(0.05)-r-DME^(0.95))₂₀₀, (FIG. 76B) (PS^(0.05)-r-DBE^(0.95))₂₀₀. These polymers correspond to each block of the lowest-grafting-density samples investigated herein. Even at large N_(bb), no evidence of microphase separation is observed, suggesting that each block is effectively homogeneous. To a first approximation, χ between the backbone and side chains does not appear significant. These data correspond to certain structures of Examples 3A and 3B.

FIGS. 77A-77Q. Raw 2D SAXS data corresponding to certain structures (e.g., System 1 or System 2; e.g., having graft density “z”, total backbone degree of polymerization “N_(bb)”, and/or period “d*”) of Examples 3A and 3B.

STATEMENTS REGARDING CHEMICAL COMPOUNDS AND NOMENCLATURE

In general, the terms and phrases used herein have their art-recognized meaning, which can be found by reference to standard texts, journal references and contexts known to those skilled in the art. The following definitions are provided to clarify their specific use in the context of the invention.

In an embodiment, a composition or compound of the invention is isolated or purified. In an embodiment, an isolated or purified compound is at least partially isolated or purified as would be understood in the art. In an embodiment, the composition or compound of the invention has a chemical purity of at least 95%, optionally for some applications at least 99%, optionally for some applications at least 99.9%, optionally for some applications at least 99.99%, and optionally for some applications at least 99.999% pure.

As used herein, the term “polymer” refers to a molecule composed of repeating structural units connected by covalent chemical bonds often characterized by a substantial number of repeating units (e.g., equal to or greater than 3 repeating units, optionally, in some embodiments equal to or greater than 10 repeating units, in some embodiments greater or equal to 30 repeating units) and a high molecular weight (e.g. greater than or equal to 10,000 Da, in some embodiments greater than or equal to 50,000 Da or greater than or equal to 100,000 Da). Polymers are commonly the polymerization product of one or more monomer precursors. The term polymer includes homopolymers, or polymers consisting essentially of a single repeating monomer subunit. The term polymer also includes copolymers which are formed when two or more different types of monomers are linked in the same polymer. Copolymers may comprise two or more monomer subunits, and include random, block, brush, brush block, alternating, segmented, grafted, tapered and other architectures. Useful polymers include organic polymers or inorganic polymers that may be in amorphous, semi-amorphous, crystalline or semi-crystalline states. Polymer side chains capable of cross linking polymers (e.g., physical cross linking) may be useful for some applications.

An “oligomer” refers to a molecule composed of repeating structural units connected by covalent chemical bonds often characterized by a number of repeating units less than that of a polymer (e.g., equal to or less than 3 repeating units) and a lower molecular weights (e.g. less than or equal to 1,000 Da) than polymers. Oligomers may be the polymerization product of one or more monomer precursors.

“Block copolymers” are a type of copolymer comprising blocks or spatially segregated domains, wherein different domains comprise different polymerized monomers, for example, including at least two chemically distinguishable blocks. Block copolymers may further comprise one or more other structural domains, such as hydrophobic groups, hydrophilic groups, thermosensitive groups, etc. In a block copolymer, adjacent blocks are constitutionally different, i.e. adjacent blocks comprise constitutional units derived from different species of monomer or from the same species of monomer but with a different composition or sequence distribution of constitutional units. Different blocks (or domains) of a block copolymer may reside on different ends or the interior of a polymer (e.g. [A][B], [B][A], [A][B][C], or [B][A][C], etc.), or may be provided in a selected sequence (e.g., [A][B][A][B], [A][B][C], or [A][B][A][C], etc.).

“Diblock copolymer” refers to block copolymer having two different polymer blocks. “Triblock copolymer” refers to a block copolymer having three different polymer blocks, including compositions in which two non-adjacent blocks are the same or similar. “Pentablock” copolymer refers to a copolymer having five different polymer including compositions in which two or more non-adjacent blocks are the same or similar.

A “graft polymer” or “graft copolymer” is a branched copolymer having a backbone, which comprises linked polymer backbone groups, and one or more branches formed, at least partially, of another polymer group, optionally further including other components such as repeating units corresponding to or having a diluent group incorporated in or attached to the backbone. A “branch” is a polymer side chain (e.g., a branched repeating unit corresponds to a repeating unit having a polymer side chain attached to a polymer backbone group). In an embodiment, the polymer backbone of a graft copolymer is a linear backbone. Each branch includes repeating polymer units. In an embodiment, the distribution of branches, or side chains, along the backbone is random, linearly gradient, non-linearly gradient, blocky, or alternating. In an example, a gradient distribution of branches is one where the frequency of branches increases from one end of the polymer to another end. In an example of a blocky distribution of branches, a repeating sequence has five or more or ten or more sequential branches are followed by five or more or ten or more non-branched repeating units. In another embodiment of a blocky distribution of branches, each type of repeating unit corresponds to only one region of the respective graft copolymer [e.g., in the case of only two types of repeating units, the graft copolymer has a first region (e.g., between a first end point and a transition point) which has repeating units only of a first type and a second region (e.g., between a second end point and the transition point) which has repeating units only of a second type]. In an example of an alternating distribution of branches, every two, or every three repeating units is a branched repeating unit. In an embodiment, a non-branched repeating unit includes a polymer backbone group and, optionally, one or more other non-polymeric groups such as one or more diluent groups. In a graft copolymer, each of the branches is independently a homopolymer or a copolymer. In an embodiment, each branch of a graft copolymer has repeating unit(s) identical to the other branches. In an embodiment, each branch of a graft copolymer is identical to the other branches. In an embodiment, a graft copolymer comprises two or more different types of branches (the repeating unit(s) of one branch being different from that of the other branch). In an embodiment, a graft copolymer has one or more types of non-branched repeating units. For example, a graft copolymer has at least a first repeating unit (e.g., non-branched, discrete, non-polymer side chain) and a second repeating unit (e.g., branched repeating unit). In an embodiment, a graft copolymer is a graft block copolymer, wherein a “graft block copolymer” is a graft copolymer having two or more different polymer blocks. In an embodiment, a polymer block of a graft block copolymer may be characterized as a graft copolymer itself. In an embodiment, each polymer block of a graft block copolymer may be characterized as a graft copolymer itself. In an embodiment, at least one polymer block of a graft block copolymer is not a graft copolymer (e.g., has no grafted polymer side chains or branches). In an embodiment, one or more polymer blocks of a graft block copolymer having two or more blocks are linear polymer blocks. A graft block copolymer may be characterized as having a distribution of polymer blocks which may be, for example, a random, a gradient, a blocky, or an alternating distribution of polymer blocks within the graft block copolymer.

As used herein, the term “discrete group” refers to a non-polymeric group. A discrete group may be a diluent group. A discrete group may be a combination of a polymer backbone group and one or more diluent groups.

The term “graft density” or “grafting density” refers to a ratio of the number of branched repeating units, of a graft copolymer or of a polymer block in a graft block copolymer, to the total number of repeating units in the graft copolymer or graft block copolymer. In other words, a graft density of 1 refers to a graft copolymer wherein each repeating unit is a branched repeating unit (i.e., 100% of the repeating units are branched—e.g., having polymer side chain groups). A graft density of 0.5 refers to a graft copolymer where half of the repeating units are branched and half of the repeating units are not branched (i.e., 50% of the repeating units are branched—e.g., having polymer side chain groups). In a graft block copolymer, each polymer block of the graft copolymer may have the same or a different graft density. In an embodiment, graft density of a graft copolymer, or a polymer block thereof, is selected from the range of greater than 0 to 1.0. In an embodiment, graft density of a graft copolymer, or a polymer block thereof, is selected from the range of 0.001 to 0.999. In an embodiment, graft density of a graft copolymer, or a polymer block thereof, is selected from the range of 0.01 to 0.99. In an embodiment, graft density of a graft copolymer, or a polymer block thereof, is at least 0.40. In an embodiment, a graft density is selected from the range of 0.4 to 0.99. In an embodiment, graft density of a graft copolymer, or a polymer block thereof, is selected from the range of 0.4 to 0.8. In an embodiment, graft density of a graft copolymer, or a polymer block thereof, is selected from the range of the range of 0.05 to 0.32, 0.34 to 0.49, 0.51 to 0.65, or 0.68 to 0.75. In an embodiment, graft density of a graft copolymer, or a polymer block thereof, is selected from the range of the range of 0.05 to 0.75.

The term “graft distribution” or “grafting distribution” refers to a distribution of branches or polymer side chains, or repeat units therewith, in a graft copolymer or a polymer block of a graft block copolymer having two or more types of repeating units (e.g., a first repeating unit and a second repeating unit; e.g., a first repeating unit, a second repeating unit, and a third repeating unit). In an embodiment, the graft distribution in graft copolymer, or polymer block thereof, is an alternating distribution, a blocky distribution, a random distribution, or a gradient distribution. In an embodiment, a gradient graft distribution is a linearly gradient distribution or a non-linearly gradient distribution. In an embodiment of an alternating graft distribution, every other one, every other two, every other three, every second, or every third repeating unit(s) is a first repeating unit. In an embodiment of a blocky graft distribution, four or more, five or more, 10 or more, 20 or more, or 50 or more are identical (e.g., a first repeating unit) and are followed by four or more, five or more, 10 or more, 20 or more, or 50 or more other identical repeating units (e.g., a second repeating unit). In another embodiment of a blocky graft distribution of branches, each type of repeating unit corresponds to only one region of the respective graft copolymer [e.g., in the case of only two types of repeating units, the graft copolymer has a first region (e.g., between a first end point and a transition point) which has repeating units only of a first type and a second region (e.g., between a second end point and the transition point) which has repeating units only of a second type]. In an embodiment of a random graft distribution, the distribution lacks long-range order, where long-range order refers to 10 or more or 20 or more repeating units. In an embodiment of a random graft distribution, the random distribution is not characterized as an alternating, a blocky, or a gradient distribution on a scale of 10 or more, or 20 or more, repeating units. In an embodiment, a gradient graft distribution is a linearly gradient distribution wherein the frequency of repeating units being branched repeating units increases linearly between one end and another end. In an embodiment, for example, a linearly gradient graft distribution is characterized as y∝mx (y is proportional to m*x), where x is a number of repeating units from a starting point (or, in other words, a distance along a polymer block from a starting end measured in increments of repeating units), y is the sum of repeating units that are branched between the starting point and x, and m is a proportionality constant, where a starting point is optionally a first repeating unit in a polymer block. In an embodiment, a gradient distribution is a non-linear distribution. In an embodiment, a non-linear gradient graft distribution is an exponential distribution characterized as y∝x^(m) (y is proportional to m{circumflex over ( )}x), where x is a number of repeating units from a starting point (or, in other words, a distance along a polymer block from a starting end measured in increments of repeating units), y is the sum of repeating units that are branched between the starting point and x, and m is a constant, where a starting point is optionally a first repeating unit in a polymer block. In an embodiment, the graft distribution of a graft copolymer or a polymer block of a graft copolymer is determined by or is dependent upon the reactivity ratio of each of the precursors of the graft copolymer, where an exemplary precursor is a macromonomer or a reactive diluent.

The term “degree of polymerization” refers to the total number of repeating units in the respective polymer or polymer block. For example, when referring to a polymer block of a graft block copolymer, degree of polymerization is the number of repeating units in said polymer block. For example, when referring to an entire graft copolymer, degree of polymerization is the number of repeating units in said entire graft copolymer.

The term “reactivity ratio”, used in reference to a chemical species which polymerizes in copolymerization reaction(s), such as a monomer, a macromonomer, or a reactive diluent, refers to a ratio of a homo-propagation rate constant to a hetero-propagation rate constant of said chemical species. For example, a monomer or diluent species M₁ and a macromonomer species M₂, which together may copolymerize, are combined. In this latter example, four reactions are possible:

M₁*+M₁→M₁M₁* (k ₁₁)

M₁*+M₂→M₁M₂* (k ₁₂)

M₂*+M₂→M₂M₂* (k ₂₂)

M₂*+M₁→M₂M₁* (k ₂₁)

where each of M₁* and M₂* refers to a radical (reactive) species chain end group of the respective species M₁ or M₂, and where k₁₁, k₁₂, k₂₂, and k₂₁ are the rate constants of the respective reactions. In this latter example, the reactivity ratio of species M₁ is

$r_{1} = \frac{k_{11}}{k_{12}}$

and the reactivity ratio of species M₂ is

$r_{2} = {\frac{k_{22}}{k_{21}}.}$

The term “initial concentration” may be used in reference to a chemical species, such as a macromonomer, participating in a reaction, such as a copolymerization reaction, where said reaction consumes said chemical species. When used in this way, the initial concentration of a chemical species is its concentration after it is introduced into the solution where the reaction takes place but immediately before the reaction initiates. In other words, the initial concentration of a species is its concentration at time=0 (“t₀”).

As used herein, the term “diluent” may refer to a “reactive diluent”, which refers to a monomeric chemical species capable of participating in a (co)polymerization reaction. Optionally, a reactive diluent is a chemical species characterized as having a low molecular weight as compared to a macromonomer. In an embodiment, the molecular weight of a diluent or a reactive diluent is less than 1,000 Da, or less than 500 Da, or less than 300 Da. In an embodiment, a reactive diluent comprises a polymer backbone precursor group and one or more diluent groups. In an embodiment, a diluent group is a discrete, non-monomer, or non-polymer group that is directly or indirectly covalently linked to a polymer backbone of a (co)polymer. In an embodiment, a graft copolymer, or a polymer block thereof, has one or more repeating units each of which comprises one or more diluent groups wherein each repeating unit that has a diluent group is a non-branched repeating unit. In an embodiment, a non-branched repeating unit is a repeating unit, of a polymer or polymer block, which lacks a polymer side chain. In an embodiment, a diluent comprises a polymer backbone precursor group having a strained olefin group, an anchor group linked to the polymer backbone precursor group, and a diluent dangling group directly or indirectly linked to the anchor group. In an embodiment, a diluent comprises a polymer backbone precursor group having a strained olefin group, an anchor group linked to the polymer backbone precursor group, a linker group linked to the anchor group, and a diluent dangling group linked to the linker group. An exemplary polymer backbone precursor group is a norbornene group. Exemplary anchor groups include, but are not limited to, groups having an alkoxy group, an ester group, an imide group, an anhydride group, and a combination thereof. Exemplary linker groups include, but are not limited to, a single bond, an oxygen, and groups having an alkyl group, an alkenylene group, an arylene group, an alkoxy group, an acyl group, a triazole group, a diazole group, a pyrazole group, and any combination thereof. Exemplary diluent dangling groups include, but are not limited to, alkyl groups such as C₁-C₁₀ alkyl groups. Exemplary diluents include, but are not limited to, racemic endo,exo-norbornenyl diesters with a methyl, an ethyl, or an n-butyl diluent dangling group linked to each ester.

The term “polymer backbone precursor group” refers to a chemical group that is incorporated into a polymer, or polymer block, backbone as a polymer backbone group as a result of a (co)polymerization reaction. In an embodiment, the polymer backbone precursor group is changed or otherwise transformed during a polymerization reaction such that the polymer backbone precursor group is not identical to the polymer backbone group which it becomes. For example, a norbornenyl group, which is an exemplary polymer backbone precursor group, may be incorporated into a polymer backbone as a divinylcyclopentane group, which is an exemplary polymer backbone group. In an embodiment, the polymer backbone precursor group is changed or otherwise transformed during a polymerization reaction such that the polymer backbone precursor group is not identical to the polymer backbone group which it becomes but one is a derivative of the other.

The term “preselected” or “pre-selected” may be used in reference to property or feature of a polymer or polymer block. In an embodiment, a preselected property or feature of a polymer, or polymer block, is a property or feature that is selected or determined (to within some degree of tolerance—e.g., to within 10% or within 5%) in advance or prior to the formation or (co)polymerization of said polymer, or polymer block. In an embodiment, a polymer or polymer block having at least one preselected property or feature is a deterministic polymer or polymer block. In an embodiment, a method for forming or synthesizing a polymer or polymer block having at least one preselected property or feature is a deterministic method for forming or synthesizing said polymer or polymer block. Exemplary properties or features, which may be preselected in accordance with the present invention, of a polymer or polymer block, include a graft density, a graft distribution, and a degree of polymerization.

The term “strained” in reference to a chemical species or group, such as a “strained olefin group”, refers to a chemical species or group that has a higher internal energy, due to strain, compared to a strain-free reference. Strain refers to a form of deformation. In an embodiment, strain refers to a compression or expansion of one or more bonds compared the lowest internal energy state equilibrium state of the bond. In an embodiment, a strain-free reference is the chemical species or group in its lowest internal energy equilibrium state.

The term “substantially equal” or “substantially equivalent”, when used in conjunction with a reference value describing a property or condition, refers to a value that is within 10%, within 5%, within 1%, or is equivalent to the provided reference value. For example, a reactivity ratio is substantially equal to 1.00 if the reactivity ratio is a value within 10%, within 5%, within 1%, or equivalent to 1.00. The term “substantially greater”, when used in conjunction with a reference value describing a property or condition, refers to a value that is at least 2%, at least 5%, or at least 10% greater than the provided reference value. For example, a reactivity ratio is substantially greater than 1.00 if the reactivity ratio is at least 2%, at least 5%, or at least 10% greater than 1.00. The term “substantially less”, when used in conjunction with a reference value describing a property or condition, refers to a value that is at least 2%, at least 5%, or at least 10% less than the provided reference value. For example, a reactivity ratio is substantially less than 1.00 if the reactivity ratio is at least 2%, at least 5%, or at least 10% less than 1.00.

The term “Grubbs' catalyst” refers to a transition metal carbene complex, known in the art as a Grubbs' catalyst, and which may be used as a catalyst for olefin metathesis. A “third-generation Grubbs' catalyst” is defined by the formula (FX100):

where X is a hydrogen or a halide (e.g., F, Cl, Br, or I).

A “bottlebrush” or “bottlebrush-type” graft copolymer is a graft copolymer, or polymer block thereof, having a high graft density and having branches extending in at least two directions. In an embodiment, a bottlebrush-type graft copolymer has a graft density of at least 0.55, at least 0.75, or at least 0.90 and has branches that extend, in total, in at least two or at least four directions from the polymer backbone. A “comb” or “comb-type” graft copolymer is a graft copolymer, or polymer block thereof, having a high graft density and having branches extending in substantially only one direction or in substantially only two directions. In an embodiment, a bottlebrush-type graft copolymer has a graft density of at least 0.55, at least 0.75, or at least 0.90 and has branches that extend substantially in only one direction or in substantially only two directions from the polymer backbone. A “linear” or “linear-type” graft copolymer is a graft copolymer, or polymer block thereof, that does not have branched repeating units, or repeating units comprising a polymer side chain.

As used herein, the term “macromonomer” refers to a high-molecular weight chemical species comprising a polymer backbone precursor group, which allows the macromonomer to act as a monomer. In an embodiment, a macromonomer comprises a polymer backbone precursor group and a polymer chain comprising at least two repeating units. In an embodiment, a macromonomer has a molecular weight of at least 500 Da, at least 1,000 Da, at least 5,000 Da, or at least 10,000 Da. In an embodiment, a macromonomer has a molecular weight selected from the range of 500 Da to 50,000 Da, or 500 Da to 10,000 Da, or 1,000 Da to 50,000 Da, or 1,000 Da to 10,000 Da. In an embodiment, a macromonomer comprises a polymer backbone precursor group having a strained olefin group, an anchor group linked to the polymer backbone precursor group, and a polymer side chain group directly or indirectly linked to the anchor group. In an embodiment, a macromonomer comprises a polymer backbone precursor group having a strained olefin group, an anchor group linked to the polymer backbone precursor group, a linker group linked to the anchor group, and a polymer side chain group linked to the linker group. An exemplary polymer backbone precursor group is a norbornene group. Exemplary anchor groups include, but are not limited to, groups having an alkoxy group, an ester group, an imide group, an anhydride group, and a combination thereof. Exemplary linker groups include, but are not limited to, a single bond, an oxygen, and groups having an alkyl group, an alkenylene group, an arylene group, an alkoxy group, an acyl group, a triazole group, a diazole group, a pyrazole group, and any combination thereof. Exemplary polymer side chain groups include, but are not limited to polystyrene (PS), polylactide (PLA), and polydimethylsiloxane (PDMS).

“Ionophobic” refers to a property of a functional group, or more generally a component of a compound, such as one or more polymer side chain groups of a brush block copolymer, which are immiscible with polar compounds, including, but not limited to, at least one of the following: water, ionic liquid, lithium salts, methanol, ethanol, and isopropanol. In a specific embodiment, for example, “ionophobic” refers to a property of a functional group, or more generally a component of a compound, such as one or more polymer side chain groups of a brush block copolymer, which are immiscible with at least one of the following water, methanol, ethanol, and isopropanol. In some embodiments, ionophobic is used to describe one or more side chains characterizing a polymer block of a copolymer that does not contribute substantially to the ionic conductivity of a copolymer or physical network thereof, but instead contributes to one or more other chemical, physical or electronic properties, such as the mechanical strength of a brush block copolymer physical network. In an embodiment, for example, polystyrene, poly(methyl methacrylate), poly(ethylene), poly(propylene), poly(butadiene), and poly(isoprene) are examples of ionophobic polymer side chains. In an embodiment, an ionophobic polymer side chain of a brush block copolymer is a hydrophobic polymer side chain.

“Ionophilic” refers to a property of a functional group, or more generally a component, of a compound, such as one or more polymer side chain groups of a brush block copolymer, which exhibit miscibility at certain relative concentrations with polar compounds including, but not limited to, at least one of the following: water, ionic liquid, lithium salts, methanol, ethanol, and isopropanol. In a specific embodiment, for example, “ionophilic” refers to a property of a functional group, or more generally a component, of a compound, such as one or more polymer side chain groups of a brush block copolymer, which exhibit miscibility with at least one of the following water, methanol, ethanol, and isopropanol. In some embodiments, “ionophilic” is used to describe one or more a side chains characterizing a polymer block of a copolymer that contributes substantially to the net ionic conductivity of a copolymer or physical network thereof. In an embodiment, for example, poly(ethylene oxide), poly(lactide), poly(N-isopropylacrylamide), and poly(pyrrolidinone) are examples of ionophilic polymer side chains. In an embodiment, an ionophilic polymer side chain of a brush block copolymer is a hydrophilic polymer side chain.

“Polymer backbone group” refers to groups that are covalently linked to make up a backbone of a polymer, such as a graft block copolymer. Polymer backbone groups may be linked to side chain groups, such as polymer side chain groups. Some polymer backbone groups useful in the present compositions are derived from polymerization of a monomer selected from the group consisting of a substituted or unsubstituted norbornene, olefin, cyclic olefin, norbornene anhydride, cyclooctene, cyclopentadiene, styrene and acrylate. Some polymer backbone groups useful in the present compositions are obtained from a ring opening metathesis polymerization (ROMP) reaction. Polymer backbones may terminate in a range of backbone terminating groups including hydrogen, C₁-C₁₀ alkyl, C₃-C₁₀ cycloalkyl, C₅-C₁₀ aryl, C₅-C₁₀ heteroaryl, C₁-C₁₀ acyl, C₁-C₁₀ hydroxyl, C₁-C₁₀ alkoxy, C₂-C₁₀ alkenyl, C₂-C₁₀ alkynyl, C₅-C₁₀ alkylaryl, —CO₂R³⁰, —CONR³¹R³², —COR³³, —SOR³⁴, —SR³⁵, —SO₂R³⁶, —OR³⁷, —SR³⁸, —NR³⁹R⁴⁰, —NR⁴¹COR⁴², C₁-C₁₀ alkyl halide, phosphonate, phosphonic acid, silane, siloxane, acrylate, or catechol; wherein each of R³⁰-R⁴² is independently hydrogen, C₁-C₁₀ alkyl or C₅-C₁₀ aryl.

“Polymer side chain group” refers to a group covalently linked to a polymer backbone group that comprises a polymer side chain, optionally imparting steric properties to the polymer. In an embodiment, for example, a polymer side chain group is characterized by a plurality of repeating units having the same, or similar, chemical composition. A polymer side chain group may be directly or indirectly linked to the polymer back bone groups. In some embodiments, polymer side chain groups provide steric bulk and/or interactions that result in an extended polymer backbone and/or a rigid polymer backbone. Some polymer side chain groups useful in the present compositions include unsubstituted or substituted polyisocyanate group, polymethacrylate group, polyacrylate group, polymethacrylamide group, polyacrylamide group, polyquinoxaline group, polyguanidine group, polysilane group, polyacetylene group, polyamino acid group, polypeptide group, polychloral group, polylactide group, polystyrene group, polyacrylate group, poly tert-butyl acrylate group, polymethyl methacrylate group, polysiloxane group, polydimethylsiloxane group, poly n-butyl acrylate group, polyethylene glycol group, polyethylene oxide group, polyethylene group, polypropylene group, polytetrafluoroethylene group, and polyvinyl chloride group. Some polymer side chain groups useful in the present compositions comprise repeating units obtained via anionic polymerization, cationic polymerization, free radical polymerization, group transfer polymerization, or ring-opening polymerization. A polymer side chain may terminate in a wide range of polymer side chain terminating groups including hydrogen, C₁-C₁₀ alkyl, C₃-C₁₀ cycloalkyl, C₅-C₁₀ aryl, C₅-C₁₀ heteroaryl, C₁-C₁₀ acyl, C₁-C₁₀ hydroxyl, C₁-C₁₀ alkoxy, C₂-C₁₀ alkenyl, C₂-C₁₀ alkynyl, C₅-C₁₀ alkylaryl, —CO₂R³⁰, —CONR³¹R³², —COR³³, —SOR³⁴, —SR³⁵, —SO₂R³⁶, —OR³⁷, —SR³⁸, —NR³⁹R⁴⁰, —NR⁴¹COR⁴², C₁-C₁₀ alkyl halide, phosphonate, phosphonic acid, silane, siloxane acrylate, or catechol; wherein each of R³⁰-R⁴² is independently hydrogen or C₁-C₅ alkyl.

As used herein, the term “brush block copolymer” refers to a block copolymer in containing at least one polymer backbone group covalently linked to at least one polymer side chain group.

“Polymer blend” refers to a mixture comprising at least one polymer, such as a block copolymer, e.g., brush block copolymer, and at least one additional component, and optionally more than one additional component. In some embodiments, for example, a polymer blend of the invention comprises a first brush block copolymer and one or more electrochemical additives. In some embodiments, for example, a polymer blend of the invention further comprises one or more additional brush block copolymers, homopolymers, copolymers, block copolymers, brush block copolymers, oligomers, electrochemical additives, solvents, metals, metal oxides, ceramics, liquids, small molecules (e.g., molecular weight less than 500 Da, optionally less than 100 Da), or any combination of these. Polymer blends useful for some applications comprise a first block copolymer, such as a brush block copolymer or a wedge-type block copolymer, and one or more additional components comprising block copolymers, brush block copolymers, wedge-type block copolymers, linear block copolymers, random copolymers, homopolymers, or any combinations of these. Polymer blends of the invention include mixture of two, three, four, five and more components.

As used herein, the term “group” may refer to a functional group of a chemical compound. Groups of the present compounds refer to an atom or a collection of atoms that are a part of the compound. Groups of the present invention may be attached to other atoms of the compound via one or more covalent bonds. Groups may also be characterized with respect to their valence state. The present invention includes groups characterized as monovalent, divalent, trivalent, etc. valence states.

As used herein, the term “substituted” refers to a compound wherein a hydrogen is replaced by another functional group, including, but not limited to: a halogen or halide, an alkyl, a cycloalkyl, an aryl, a heteroaryl, an acyl, an alkoxy, an alkenyl, an alkynyl, an alkylaryl, an arylene, a heteroarylene, an alkenylene, a cycloalkenylene, an alkynylene, a hydroxyl (—OH), a carbonyl (RCOR′), a sulfide (e.g., RSR′), a phosphate (ROP(═O)(OH)₂), an azo (RNNR′), a cyanate (ROCN), an amine (e.g., primary, secondary, or tertiary), an imine (RC(═NH)R′), a nitrile (RCN), a pyridinyl (or pyridyl), a diamine, a triamine, an azide, a diimine, a triimine, an amide, a diimide, or an ether (ROR′); where each of R and R′ is independently a hydrogen or a substituted or unsubstituted alkyl group, aryl group, alkenyl group, or a combination of these. Optional substituent functional groups are also described below. In some embodiments, the term substituted refers to a compound wherein more than one hydrogen is replaced by another functional group, such as a halogen group.

Unless otherwise specified, the term “molecular weight” refers to an average molecular weight. Unless otherwise specified, the term “average molecular weight,” refers to number-average molecular weight. Number average molecular weight is defined as the total weight of a sample volume divided by the number of molecules within the sample. As is customary and well known in the art, peak average molecular weight and weight average molecular weight may also be used to characterize the molecular weight of the distribution of polymers within a sample.

The term “weight-average molecular weight” (M_(w)) refers to the average molecular weight defined as the sum of the products of the molecular weight of each polymer molecule (M_(i)) multiplied by its weight fraction (w_(i)): M_(w)=Σw_(i)M_(i). As is customary and well known in the art, peak average molecular weight and number average molecular weight may also be used to characterize the molecular weight of the distribution of polymers within a sample.

As is customary and well known in the art, hydrogen atoms in formulas (FX1a)-(FX12f) are not always explicitly shown, for example, hydrogen atoms bonded to the carbon atoms of aromatic, heteroaromatic, and alicyclic rings are not always explicitly shown in formulas (FX1a)-(FX12f). The structures provided herein, for example in the context of the description of formulas (FX1a)-(FX12f) and schematics and structures in the drawings, are intended to convey to one of reasonable skill in the art the chemical composition of compounds of the methods and compositions of the invention, and as will be understood by one of skill in the art, the structures provided do not indicate the specific positions and/or orientations of atoms and the corresponding bond angles between atoms of these compounds.

As used herein, the terms “alkylene” and “alkylene group” are used synonymously and refer to a divalent group derived from an alkyl group as defined herein. The invention includes compounds having one or more alkylene groups. Alkylene groups in some compounds function as linking and/or spacer groups. Compounds of the invention may have substituted and/or unsubstituted C₁-C₂₀ alkylene, C₁-C₁₀ alkylene and C₁-C₅ alkylene groups, for example, as one or more linking groups (e.g. L¹-L⁶).

As used herein, the terms “cycloalkylene” and “cycloalkylene group” are used synonymously and refer to a divalent group derived from a cycloalkyl group as defined herein. The invention includes compounds having one or more cycloalkylene groups. Cycloalkyl groups in some compounds function as linking and/or spacer groups. Compounds of the invention may have substituted and/or unsubstituted C₃-C₂₀ cycloalkylene, C₃-C₁₀ cycloalkylene and C₃-C₅ cycloalkylene groups, for example, as one or more linking groups (e.g. L¹-L⁶).

As used herein, the terms “arylene” and “arylene group” are used synonymously and refer to a divalent group derived from an aryl group as defined herein. The invention includes compounds having one or more arylene groups. In some embodiments, an arylene is a divalent group derived from an aryl group by removal of hydrogen atoms from two intra-ring carbon atoms of an aromatic ring of the aryl group. Arylene groups in some compounds function as linking and/or spacer groups. Arylene groups in some compounds function as chromophore, fluorophore, aromatic antenna, dye and/or imaging groups. Compounds of the invention include substituted and/or unsubstituted C₃-C₃₀ arylene, C₃-C₂₀ arylene, C₃-C₁₀ arylene and C₁-C₅ arylene groups, for example, as one or more linking groups (e.g. L¹-L⁶).

As used herein, the terms “heteroarylene” and “heteroarylene group” are used synonymously and refer to a divalent group derived from a heteroaryl group as defined herein. The invention includes compounds having one or more heteroarylene groups. In an embodiment, a heteroarylene is a divalent group derived from a heteroaryl group by removal of hydrogen atoms from two intra-ring carbon atoms or intra-ring nitrogen atoms of a heteroaromatic or aromatic ring of the heteroaryl group. Heteroarylene groups in some compounds function as linking and/or spacer groups. Heteroarylene groups in some compounds function as chromophore, aromatic antenna, fluorophore, dye and/or imaging groups. Compounds of the invention include substituted and/or unsubstituted C₃-C₃₀ heteroarylene, C₃-C₂₀ heteroarylene, C₁-C₁₀ heteroarylene and C₃-C₅ heteroarylene groups, for example, as one or more linking groups (e.g. L¹-L⁶).

As used herein, the terms “alkenylene” and “alkenylene group” are used synonymously and refer to a divalent group derived from an alkenyl group as defined herein. The invention includes compounds having one or more alkenylene groups. Alkenylene groups in some compounds function as linking and/or spacer groups. Compounds of the invention include substituted and/or unsubstituted C₂-C₂₀ alkenylene, C₂-C₁₀ alkenylene and C₂-C₅ alkenylene groups, for example, as one or more linking groups (e.g. L¹-L⁶).

As used herein, the terms “cylcoalkenylene” and “cylcoalkenylene group” are used synonymously and refer to a divalent group derived from a cylcoalkenyl group as defined herein. The invention includes compounds having one or more cylcoalkenylene groups. Cycloalkenylene groups in some compounds function as linking and/or spacer groups. Compounds of the invention include substituted and/or unsubstituted C₃-C₂₀ cylcoalkenylene, C₃-C₁₀ cylcoalkenylene and C₃-C₅ cylcoalkenylene groups, for example, as one or more linking groups (e.g. L¹-L⁶).

As used herein, the terms “alkynylene” and “alkynylene group” are used synonymously and refer to a divalent group derived from an alkynyl group as defined herein. The invention includes compounds having one or more alkynylene groups. Alkynylene groups in some compounds function as linking and/or spacer groups. Compounds of the invention include substituted and/or unsubstituted C₂-C₂₀ alkynylene, C₂-C₁₀ alkynylene and C₂-C₅ alkynylene groups, for example, as one or more linking groups (e.g. L¹-L⁶).

As used herein, the term “halo” refers to a halogen group such as a fluoro (—F), chloro (—Cl), bromo (—Br), iodo (—I) or astato (—At).

The term “heterocyclic” refers to ring structures containing at least one other kind of atom, in addition to carbon, in the ring. Examples of such heteroatoms include nitrogen, oxygen and sulfur. Heterocyclic rings include heterocyclic alicyclic rings and heterocyclic aromatic rings. Examples of heterocyclic rings include, but are not limited to, pyrrolidinyl, piperidyl, imidazolidinyl, tetrahydrofuryl, tetrahydrothienyl, furyl, thienyl, pyridyl, quinolyl, isoquinolyl, pyridazinyl, pyrazinyl, indolyl, imidazolyl, oxazolyl, thiazolyl, pyrazolyl, pyridinyl, benzoxadiazolyl, benzothiadiazolyl, triazolyl and tetrazolyl groups. Atoms of heterocyclic rings can be bonded to a wide range of other atoms and functional groups, for example, provided as substituents.

The term “carbocyclic” refers to ring structures containing only carbon atoms in the ring. Carbon atoms of carbocyclic rings can be bonded to a wide range of other atoms and functional groups, for example, provided as substituents.

The term “alicyclic ring” refers to a ring, or plurality of fused rings, that is not an aromatic ring. Alicyclic rings include both carbocyclic and heterocyclic rings.

The term “aromatic ring” refers to a ring, or a plurality of fused rings, that includes at least one aromatic ring group. The term aromatic ring includes aromatic rings comprising carbon, hydrogen and heteroatoms. Aromatic ring includes carbocyclic and heterocyclic aromatic rings. Aromatic rings are components of aryl groups.

The term “fused ring” or “fused ring structure” refers to a plurality of alicyclic and/or aromatic rings provided in a fused ring configuration, such as fused rings that share at least two intra ring carbon atoms and/or heteroatoms.

As used herein, the term “alkoxyalkyl” refers to a substituent of the formula alkyl-O-alkyl.

As used herein, the term “polyhydroxyalkyl” refers to a substituent having from 2 to 12 carbon atoms and from 2 to 5 hydroxyl groups, such as the 2,3-dihydroxypropyl, 2,3,4-trihydroxybutyl or 2,3,4,5-tetrahydroxypentyl residue.

As used herein, the term “polyalkoxyalkyl” refers to a substituent of the formula alkyl-(alkoxy)_(n)-alkoxy wherein n is an integer from 1 to 10, preferably 1 to 4, and more preferably for some embodiments 1 to 3.

Amino acids include glycine, alanine, valine, leucine, isoleucine, methionine, proline, phenylalanine, tryptophan, asparagine, glutamine, glycine, serine, threonine, serine, rhreonine, asparagine, glutamine, tyrosine, cysteine, lysine, arginine, histidine, aspartic acid and glutamic acid. As used herein, reference to “a side chain residue of a natural α-amino acid” specifically includes the side chains of the above-referenced amino acids. Peptides are comprised of two or more amino-acid connected via peptide bonds.

Alkyl groups include straight-chain, branched and cyclic alkyl groups. Alkyl groups include those having from 1 to 30 carbon atoms. Alkyl groups include small alkyl groups having 1 to 3 carbon atoms. Alkyl groups include medium length alkyl groups having from 4-10 carbon atoms. Alkyl groups include long alkyl groups having more than 10 carbon atoms, particularly those having 10-30 carbon atoms. The term cycloalkyl specifically refers to an alky group having a ring structure such as ring structure comprising 3-30 carbon atoms, optionally 3-20 carbon atoms and optionally 2-10 carbon atoms, including an alkyl group having one or more rings. Cycloalkyl groups include those having a 3-, 4-, 5-, 6-, 7-, 8-, 9- or 10-member carbon ring(s) and particularly those having a 3-, 4-, 5-, 6-, 7-, or 8-member ring(s). The carbon rings in cycloalkyl groups can also carry alkyl groups. Cycloalkyl groups can include bicyclic and tricycloalkyl groups. Alkyl groups are optionally substituted. Substituted alkyl groups include among others those which are substituted with aryl groups, which in turn can be optionally substituted. Specific alkyl groups include methyl, ethyl, n-propyl, iso-propyl, cyclopropyl, n-butyl, s-butyl, t-butyl, cyclobutyl, n-pentyl, branched-pentyl, cyclopentyl, n-hexyl, branched hexyl, and cyclohexyl groups, all of which are optionally substituted. Substituted alkyl groups include fully halogenated or semihalogenated alkyl groups, such as alkyl groups having one or more hydrogens replaced with one or more fluorine atoms, chlorine atoms, bromine atoms and/or iodine atoms. Substituted alkyl groups include fully fluorinated or semifluorinated alkyl groups, such as alkyl groups having one or more hydrogens replaced with one or more fluorine atoms. An alkoxy group is an alkyl group that has been modified by linkage to oxygen and can be represented by the formula R—O and can also be referred to as an alkyl ether group. Examples of alkoxy groups include, but are not limited to, methoxy, ethoxy, propoxy, butoxy and heptoxy. Alkoxy groups include substituted alkoxy groups wherein the alky portion of the groups is substituted as provided herein in connection with the description of alkyl groups. As used herein MeO— refers to CH₃O—. Compositions of some embodiments of the invention comprise alkyl groups as terminating groups, such as polymer backbone terminating groups and/or polymer side chain terminating groups. Substituted alkyl groups may include substitution to incorporate one or more silyl groups, for example wherein one or more carbons are replaced by Si.

Alkenyl groups include straight-chain, branched and cyclic alkenyl groups. Alkenyl groups include those having 1, 2 or more double bonds and those in which two or more of the double bonds are conjugated double bonds. Alkenyl groups include those having from 2 to 20 carbon atoms. Alkenyl groups include small alkenyl groups having 2 to 3 carbon atoms. Alkenyl groups include medium length alkenyl groups having from 4-10 carbon atoms. Alkenyl groups include long alkenyl groups having more than 10 carbon atoms, particularly those having 10-20 carbon atoms. Cycloalkenyl groups include those in which a double bond is in the ring or in an alkenyl group attached to a ring. The term cycloalkenyl specifically refers to an alkenyl group having a ring structure, including an alkenyl group having a 3-, 4-, 5-, 6-, 7-, 8-, 9- or 10-member carbon ring(s) and particularly those having a 3-, 4-, 5-, 6- or 7-member ring(s). The carbon rings in cycloalkenyl groups can also carry alkyl groups. Cycloalkenyl groups can include bicyclic and tricyclic alkenyl groups. Alkenyl groups are optionally substituted. Substituted alkenyl groups include among others those which are substituted with alkyl or aryl groups, which groups in turn can be optionally substituted. Specific alkenyl groups include ethenyl, prop-1-enyl, prop-2-enyl, cycloprop-1-enyl, but-1-enyl, but-2-enyl, cyclobut-1-enyl, cyclobut-2-enyl, pent-1-enyl, pent-2-enyl, branched pentenyl, cyclopent-1-enyl, hex-1-enyl, branched hexenyl, cyclohexenyl, all of which are optionally substituted. Substituted alkenyl groups include fully halogenated or semihalogenated alkenyl groups, such as alkenyl groups having one or more hydrogens replaced with one or more fluorine atoms, chlorine atoms, bromine atoms and/or iodine atoms. Substituted alkenyl groups include fully fluorinated or semifluorinated alkenyl groups, such as alkenyl groups having one or more hydrogen atoms replaced with one or more fluorine atoms. Compositions of some embodiments of the invention comprise alkenyl groups as terminating groups, such as polymer backbone terminating groups and/or polymer side chain terminating groups.

Aryl groups include groups having one or more 5-, 6- 7-, or 8-member aromatic rings, including heterocyclic aromatic rings. The term heteroaryl specifically refers to aryl groups having at least one 5-, 6- 7-, or 8-member heterocyclic aromatic rings. Aryl groups can contain one or more fused aromatic rings, including one or more fused heteroaromatic rings, and/or a combination of one or more aromatic rings and one or more nonaromatic rings that may be fused or linked via covalent bonds. Heterocyclic aromatic rings can include one or more N, O, or S atoms in the ring. Heterocyclic aromatic rings can include those with one, two or three N atoms, those with one or two O atoms, and those with one or two S atoms, or combinations of one or two or three N, O or S atoms. Aryl groups are optionally substituted. Substituted aryl groups include among others those that are substituted with alkyl or alkenyl groups, which groups in turn can be optionally substituted. Specific aryl groups include phenyl, biphenyl groups, pyrrolidinyl, imidazolidinyl, tetrahydrofuryl, tetrahydrothienyl, furyl, thienyl, pyridyl, quinolyl, isoquinolyl, pyridazinyl, pyrazinyl, indolyl, imidazolyl, oxazolyl, thiazolyl, pyrazolyl, pyridinyl, benzoxadiazolyl, benzothiadiazolyl, and naphthyl groups, all of which are optionally substituted. Substituted aryl groups include fully halogenated or semihalogenated aryl groups, such as aryl groups having one or more hydrogens replaced with one or more fluorine atoms, chlorine atoms, bromine atoms and/or iodine atoms. Substituted aryl groups include fully fluorinated or semifluorinated aryl groups, such as aryl groups having one or more hydrogens replaced with one or more fluorine atoms. Aryl groups include, but are not limited to, aromatic group-containing or heterocylic aromatic group-containing groups corresponding to any one of the following: benzene, naphthalene, naphthoquinone, diphenylmethane, fluorene, anthracene, anthraquinone, phenanthrene, tetracene, tetracenedione, pyridine, quinoline, isoquinoline, indoles, isoindole, pyrrole, imidazole, oxazole, thiazole, pyrazole, pyrazine, pyrimidine, purine, benzimidazole, furans, benzofuran, dibenzofuran, carbazole, acridine, acridone, phenanthridine, thiophene, benzothiophene, dibenzothiophene, xanthene, xanthone, flavone, coumarin, azulene or anthracycline. As used herein, a group corresponding to the groups listed above expressly includes an aromatic or heterocyclic aromatic group, including monovalent, divalent and polyvalent groups, of the aromatic and heterocyclic aromatic groups listed herein are provided in a covalently bonded configuration in the compounds of the invention at any suitable point of attachment. In embodiments, aryl groups contain between 5 and 30 carbon atoms. In embodiments, aryl groups contain one aromatic or heteroaromatic six-member ring and one or more additional five- or six-member aromatic or heteroaromatic ring. In embodiments, aryl groups contain between five and eighteen carbon atoms in the rings. Aryl groups optionally have one or more aromatic rings or heterocyclic aromatic rings having one or more electron donating groups, electron withdrawing groups and/or targeting ligands provided as substituents. Compositions of some embodiments of the invention comprise aryl groups as terminating groups, such as polymer backbone terminating groups and/or polymer side chain terminating groups.

Arylalkyl groups are alkyl groups substituted with one or more aryl groups wherein the alkyl groups optionally carry additional substituents and the aryl groups are optionally substituted. Specific alkylaryl groups are phenyl-substituted alkyl groups, e.g., phenylmethyl groups. Alkylaryl groups are alternatively described as aryl groups substituted with one or more alkyl groups wherein the alkyl groups optionally carry additional substituents and the aryl groups are optionally substituted. Specific alkylaryl groups are alkyl-substituted phenyl groups such as methylphenyl. Substituted arylalkyl groups include fully halogenated or semihalogenated arylalkyl groups, such as arylalkyl groups having one or more alkyl and/or aryl groups having one or more hydrogens replaced with one or more fluorine atoms, chlorine atoms, bromine atoms and/or iodine atoms. Compositions of some embodiments of the invention comprise arylalkyl groups as terminating groups, such as polymer backbone terminating groups and/or polymer side chain terminating groups.

As to any of the groups described herein which contain one or more substituents, it is understood that such groups do not contain any substitution or substitution patterns which are sterically impractical and/or synthetically non-feasible. In addition, the compounds of this invention include all stereochemical isomers arising from the substitution of these compounds. Optional substitution of alkyl groups includes substitution with one or more alkenyl groups, aryl groups or both, wherein the alkenyl groups or aryl groups are optionally substituted. Optional substitution of alkenyl groups includes substitution with one or more alkyl groups, aryl groups, or both, wherein the alkyl groups or aryl groups are optionally substituted. Optional substitution of aryl groups includes substitution of the aryl ring with one or more alkyl groups, alkenyl groups, or both, wherein the alkyl groups or alkenyl groups are optionally substituted.

Optional substituents for any alkyl, alkenyl and aryl group includes substitution with one or more of the following substituents, among others:

halogen, including fluorine, chlorine, bromine or iodine;

pseudohalides, including —CN;

-   -   —COOR where R is a hydrogen or an alkyl group or an aryl group         and more specifically where R is a methyl, ethyl, propyl, butyl,         or phenyl group all of which groups are optionally substituted;     -   —COR where R is a hydrogen or an alkyl group or an aryl group         and more specifically where R is a methyl, ethyl, propyl, butyl,         or phenyl group all of which groups are optionally substituted;     -   —CON(R)₂ where each R, independently of each other R, is a         hydrogen or an alkyl group or an aryl group and more         specifically where R is a methyl, ethyl, propyl, butyl, or         phenyl group all of which groups are optionally substituted; and         where R and R can form a ring which can contain one or more         double bonds and can contain one or more additional carbon         atoms;     -   —OCON(R)₂ where each R, independently of each other R, is a         hydrogen or an alkyl group or an aryl group and more         specifically where R is a methyl, ethyl, propyl, butyl, or         phenyl group all of which groups are optionally substituted; and         where R and R can form a ring which can contain one or more         double bonds and can contain one or more additional carbon         atoms;     -   —N(R)₂ where each R, independently of each other R, is a         hydrogen, or an alkyl group, or an acyl group or an aryl group         and more specifically where R is a methyl, ethyl, propyl, butyl,         phenyl or acetyl group, all of which are optionally substituted;         and where R and R can form a ring which can contain one or more         double bonds and can contain one or more additional carbon         atoms;     -   —SR, where R is hydrogen or an alkyl group or an aryl group and         more specifically where R is hydrogen, methyl, ethyl, propyl,         butyl, or a phenyl group, which are optionally substituted;

—SO₂R, or —SOR where R is an alkyl group or an aryl group and more specifically where R is a methyl, ethyl, propyl, butyl, or phenyl group, all of which are optionally substituted;

-   -   —OCOOR where R is an alkyl group or an aryl group;     -   —SO₂N(R)₂ where each R, independently of each other R, is a         hydrogen, or an alkyl group, or an aryl group all of which are         optionally substituted and wherein R and R can form a ring which         can contain one or more double bonds and can contain one or more         additional carbon atoms; and     -   —OR where R is H, an alkyl group, an aryl group, or an acyl         group all of which are optionally substituted. In a particular         example R can be an acyl yielding —OCOR″ where R″ is a hydrogen         or an alkyl group or an aryl group and more specifically where         R″ is methyl, ethyl, propyl, butyl, or phenyl groups all of         which groups are optionally substituted.

Specific substituted alkyl groups include haloalkyl groups, particularly trihalomethyl groups and specifically trifluoromethyl groups. Specific substituted aryl groups include mono-, di-, tri, tetra- and pentahalo-substituted phenyl groups; mono-, di-, tri-, tetra-, penta-, hexa-, and hepta-halo-substituted naphthalene groups; 3- or 4-halo-substituted phenyl groups, 3- or 4-alkyl-substituted phenyl groups, 3- or 4-alkoxy-substituted phenyl groups, 3- or 4-RCO-substituted phenyl, 5- or 6-halo-substituted naphthalene groups. More specifically, substituted aryl groups include acetylphenyl groups, particularly 4-acetylphenyl groups; fluorophenyl groups, particularly 3-fluorophenyl and 4-fluorophenyl groups; chlorophenyl groups, particularly 3-chlorophenyl and 4-chlorophenyl groups; methylphenyl groups, particularly 4-methylphenyl groups; and methoxyphenyl groups, particularly 4-methoxyphenyl groups.

As to any of the above groups which contain one or more substituents, it is understood that such groups do not contain any substitution or substitution patterns which are sterically impractical and/or synthetically non-feasible.

Many of the molecules disclosed herein contain one or more ionizable groups. Ionizable groups include groups from which a proton can be removed (e.g., —COOH) or added (e.g., amines) and groups that can be quaternized (e.g., amines). All possible ionic forms of such molecules and salts thereof are intended to be included individually in the disclosure herein. With regard to salts of the compounds herein, one of ordinary skill in the art can select from among a wide variety of available counterions that are appropriate for preparation of salts of this invention for a given application. In specific applications, the selection of a given anion or cation for preparation of a salt can result in increased or decreased solubility of that salt.

The compounds of this invention can contain one or more chiral centers. Accordingly, this invention is intended to include racemic mixtures, diastereomers, enantiomers, tautomers and mixtures enriched in one or more stereoisomer. The scope of the invention as described and claimed encompasses the racemic forms of the compounds as well as the individual enantiomers and non-racemic mixtures thereof.

As used herein, the term “polydispersity index” of a polymer can be calculated as M_(w)/M_(n), where M_(w) is the weight-averaged molar mass and M_(n) is the number-averaged molar mass of the polymer. In an embodiment, the polydispersity index of a graft copolymer of the present invention is selected from the range of 1.00 to 1.20, or 1.00 to 1.10, or 1.00 to 1.05.

As used herein, the term “thermosensitive” refers to a temperature-responsive or thermoresponsive polymer that exhibits significant and, optionally discontinuous, change of their physical properties with temperature, such as a change in phase, or physical property.

As used herein, the term “% w/v” refers to a measurement of concentration wherein 1% w/v equates to 1g of solute per a total volume of 100 mL of solution.

The terms “non-aqueous solvent”, “nonaqueous solvent”, and “organic solvent” may be used interchangeably and refer to a non-water liquid in which may dissolve a solute, such as a metal-coordination complex. The non-aqueous solvent may include small amounts of water, such that the water is a solute or impurity dissolved in the non-aqueous solvent. The non-aqueous solvent may include small amounts of water but such that the predominant phase of the solution is the non-water liquid and the solute(s) remains substantially dissolved in the non-water phase. In some of the embodiments disclosed herein, non-aqueous solvent may be acetonitrile, 2-methyltetrahydrofuran, tetrahydrofuran, nitromethane, dichloromethane, propylene carbonate, liquid sulfur dioxide (l-SO₂), dimethyl formamide, ionic liquid, perfluorinated liquid, or any combination of these.

The term “self-assembly” refers to a process in which individual elements assemble into a network, optionally a crystalline network, or organized structure without external direction. In an embodiment, self-assembly leads to a decrease in entropy of a system. In an embodiment, a self-assembly process is an annealing process, wherein a disordered system takes on a more ordered arrangement. In an embodiment, self-assembly may be induced, or initiated, via temperature and/or pressure. In an embodiment, self-assembly is induced or initiated via pressure, either due to a change in pressure, such as a pressure increase, and/or due to reaching a particular pressure at which self-assembly occurs. Self-assembly induced or initiated via pressure may be referred to as pressure annealing. In an embodiment, pressure annealing is performed by applying a contact pressure on a material or a layer thereof. In an embodiment, self-assembly is induced or initiated via temperature, either due to a change in temperature, such as a temperature increase, and/or due to reaching a particular temperature at which self-assembly occurs. Self-assembly induced or initiated via temperature may be referred to as temperature annealing. A “self-assembled structure” is a structure or network formed by self-assembly. In an embodiment, self-assembly is a polymer crystallization process. The Gibbs free energy of the self-assembled structure is lower than of the sum of the individual components in their non-organized arrangement prior to self-assembly under otherwise identical conditions (e.g., temperature and pressure). In an embodiment, entropy of a self-assembled structure is lower than that of the sum of the individual components in their non-organized arrangement prior to self-assembly under otherwise identical conditions (e.g., temperature and pressure). In an embodiment, a self-assembled structure is a polymer network formed from a plurality of polymers, such as graft block copolymers. In an embodiment, a self-assembled structure is an amorphous, a semi-crystalline, or a crystalline polymer network or structure. In an embodiment, a self-assembled structure is a semi-crystalline or a crystalline polymer network or structure. In an embodiment, a self-assembled structure is a semi-crystalline polymer structure having a degree of crystallinity selected from the range of 10% to 90%, or 10% to 80%. In an embodiment, a self-assembled structure is a polymer network having a lamellar structure. In an embodiment, a lamellar structure is a rectangular sheet structure having a finite length, width, and thickness. A lamellar structure or network may be referred to as a lamella. A polymer network having a lamellar structure may be characterized as having a period, which refers to a characteristic size dimension (e.g., thickness) of a unit cell or repeating structural unit of the lamellar structure. A characteristic size dimension may be a size of a repeating structure unit in the direction of repetition. For example, a lamellar sheet characterized as having a stack of parallel [A] and [B] planes (e.g., [A][B][A][B], etc.), where each [A] plane is substantially identical to other [A] planes and each [B] plane is substantially identical to other [B] planes, may be characterized as having a period corresponding to the sum thickness of one [A][B] sequence (or, thickness of one [A] plane and one [B] plane).

The term “photonic crystal” refers to a periodic structure that affects the motion of photons. In an embodiment, a photonic crystal is at least partially or is substantially formed of a polymer network or polymer structure, such as a lamellar polymer structure. In an embodiment, a photonic crystal is capable of or is configured to reflect at least a portion of wavelengths of the visible light spectrum. In an embodiment, a photonic crystal is capable of or is configured to reflect at least a portion of wavelengths of the infrared light spectrum. In an embodiment, a photonic crystal is capable of or is configured to reflect at least a portion of wavelengths of the visible light spectrum and of the infrared light spectrum.

The term “matrix-sphere structure” refers to a structure characterized as comprising a matrix having element A and spheres having element B. In an embodiment, a matrix-sphere structure refers to a self-assembled structure having a plurality of graft block copolymers where a first polymer block of each of the plurality of graft block copolymer collectively forms a matrix and a second polymer block of each of the plurality of graft block copolymer collectively forms one or more spheres within the matrix.

The term “matrix-gyroid structure” refers to a structure characterized as comprising a matrix having element A and gyroids having element B. In an embodiment, a matrix-gyroid structure refers to a self-assembled structure having a plurality of graft block copolymers where a first polymer block of each of the plurality of graft block copolymer collectively forms a matrix and a second polymer block of each of the plurality of graft block copolymer collectively forms one or more gyroids within the matrix.

The term “matrix-cylinder structure” refers to a structure characterized as comprising a matrix having element A and cylinders having element B. In an embodiment, a matrix-cylinders structure refers to a self-assembled structure having a plurality of graft block copolymers where a first polymer block of each of the plurality of graft block copolymer collectively forms a matrix and a second polymer block of each of the plurality of graft block copolymer collectively forms one or more cylinders within the matrix.

The term “total thickness in a transverse direction” may refer to a polymer structure having periodicity such that the direction of periodicity is a transverse direction.

DETAILED DESCRIPTION OF THE INVENTION

In general, the terms and phrases used herein have their art-recognized meaning, which can be found by reference to standard texts, journal references and contexts known to those skilled in the art. The following definitions are provided to clarify their specific use in the context of the invention.

Example 1: Control of Grafting Density and Distribution in Graft Polymers by Living Ring-Opening Metathesis Copolymerization

We provide effective new methods that allow for facile control of the polymer sequences and architectures by ring-opening metathesis copolymerization of a pair of cyclic olefins. Mediated by a highly active ruthenium metathesis catalyst, the monomer pair may be strategically designed to have preselected properties such that the copolymerization yields a random or gradient sequence. The copolymerization sequence, dictated by the reactivity ratios of the monomer pair, may be easily and reliably determined by a non-linear curving-fitting method we developed (see the attached paper). In this example, we demonstrate that copolymerization reactions of a diluent (endo,exo-norbornenyl-dimethylester “DME”, -diethylester “DE”E, or -di-n-butylester “DBE”) with a norbornene-functionalized macromonomer (polystyrene “PS”, polylactide “PLA”, or polydimethylsiloxane “PDMS”) may generate random (r₁≈r₂≈1) or gradient (r₁<1<r₂; r₁>1>r₂) sequences. These results show that the ring-opening metathesis copolymerization methods of the present example can be exploited in the context of side chain density and distribution control, providing new opportunities for designing architecturally complex polymers spanning the linear-to-bottlebrush regimes.

Abstract: Control over polymer sequence and architecture is important to both understanding structure-property relationships and designing functional materials. Accordingly, we provide a new synthetic approach that enables facile manipulation of the density and distribution of grafts in polymers via living ring-opening metathesis polymerization (ROMP). In this example, discrete endo,exo-norbornenyl dialkylesters (dimethyl (“DME”), diethyl (“DEE”), di-n-butyl (“DBE”)) are strategically designed to copolymerize with a norbornene-functionalized polystyrene (“PS”), polylactide (“PLA”), or polydimethylsiloxane (“PDMS”) macromonomer mediated by a 3^(rd) generation Grubbs' catalyst (“G3”). The small-molecule diesters act as diluents that increase the average distance between grafted side chains, generating polymers with variable grafting density. The grafting density (number of side chains/number of norbornene monomers) is straightforwardly controlled by the macromonomer/diluent feed ratio. To gain insight into the copolymer sequence and architecture, self-propagation and cross-propagation rate constants are determined according to a terminal copolymerization model. These kinetic analyses show that copolymerizing a macromonomer/diluent pair with evenly matched self-propagation rate constants favors randomly distributed side chains. As the disparity between macromonomer and diluent homopolymerization rates increases, the reactivity ratios depart from unity, leading to an increase in gradient tendency. To demonstrate the effectiveness of our methods, an array of monodisperse polymers (PLA^(x)-ran-DME^(1-x))_(n) bearing various grafting densities (x=1.0, 0.75, 0.5, 0.25) and total backbone degrees of polymerization (n=167, 133, 100, 67, 33) are synthesized in this example. The approach disclosed in this example constitutes a powerful strategy for the synthesis of polymers spanning the linear-to-bottlebrush regimes with controlled and preselected grafting density and/or side chain distribution, molecular attributes that dictate micro- and macroscopic properties.

Introduction: Bottlebrush polymers are a subset of graft polymers that consist of a polymer backbone bearing densely grafted side chains.¹ The steric demands exerted by side chains encourage the backbone to adopt an extended wormlike conformation,² rendering distinct mechanical and physical features uncharacteristic of linear analogues.³ Numerous studies have accordingly leveraged the unique attributes of bottlebrush polymers to address challenges in diverse applications including drug delivery,⁴ surface coatings,⁵ photolithography,⁶ pressure sensors,⁷ transport,⁸ energy storage,⁹ and photonics.¹⁰ These achievements are facilitated by a host of grafting-to, grafting-from, and grafting-through polymerization methodologies, enabling control over structural parameters such as the backbone degree of polymerization, side chain degree of polymerization, molar mass dispersity, and chemical functionality.

Despite prior advances, systematic variation of grafting density exhaustively spanning the linear-to-bottlebrush regimes remained synthetically challenging.¹¹ Grafting density is of fundamental importance in shaping the mechanical¹²/physical¹³ properties, self-assembly,¹⁴ and stimuli-responsiveness¹⁵ exhibited by graft polymers. We provide an effective and efficient synthetic protocol to modify grafting density which increases understanding of the structure-property-function relationships¹⁶ in graft polymers. Matyjaszewski previously reported the copolymerization of an acryloyl-functionalized macromonomer with n-butyl acrylate using atom transfer radical polymerization (ATRP).¹⁷ Matyjaszewski elegantly illustrated the role of n-butyl acrylate as a diluent that served to increase the average distance between grafting points. However, harsh conditions and prolonged reaction times were required in Matyjaszewski, and low backbone degrees of polymerization could be achieved at high grafting density due to the steric profile of the macromonomers. Another method described by Kamigaito employed radical copolymerization of limonene and maleimide derivatives, generating an ABB alternating propagation sequence.¹⁸ The limonene or maleimide derivative was selectively functionalized to subsequently enable a “grafting-from” installation of poly(methyl methacrylate) side chains. However, Kamigaito yields polymers with precisely 33% or 67% grafting densities and with high molar mass dispersity (Ð≈1.7).

We show that a living ring-opening metathesis polymerization (ROMP)¹⁹ of the present invention is an approach that may circumvent the aforementioned challenges. Our method harnesses the many advantages of living ROMP including 1) mild reaction conditions, 2) low molar mass dispersity, 3) uniform side chain lengths, 4) living character with tunable backbone degrees of polymerization, and 5) functional group tolerance. We herein provide the first demonstration that ROMP can be exploited for preselected grafting density control. In this example, monodisperse polymers with grafting densities spanning the linear, comb, and bottlebrush regimes are easily accessible by copolymerization reactions of a norbornene-functionalized macromonomer with a discrete small-molecule diluent in different feed ratios (FIG. 2). In-depth kinetic analyses reveal that the distribution (random or gradient) of grafts is adjusted by simple modifications to the diluent ester substituents. The methods of the present invention therefore constitute an effective strategy in controlling polymer architecture,²⁰ providing new opportunities for polymer design and applications.

Monomer design. In pursuit of this approach, we determine the homopolymerization kinetics of macromonomers and diluents bearing polymerizable end groups. Cyclic olefinic monomers may favor alternating sequences,²¹ but since strict alternation may limit grafting density to 50% and preclude control over graft distribution, cyclic olefinic monomers are not used in this example. Instead, norbornene-functionalized derivatives, which rarely result in alternating polynorbornene,²² are selected for the present example. Relief of the high ring strain in norbornene, mediated by highly active ruthenium metathesis catalysts, enables grafting-through ROMP to produce well-defined bottlebrush polymers.²³ We also note that random copolymerization of norbornenes has been previously inferred,^(23b,24) suggesting potential opportunities for advanced sequence control. However, quantitative sequence determination has been lacking in prior work. With this context in mind, ω-norbornenyl polystyrene (“PS”, M_(n)=3990 g/mol), polylactide (“PLA”, M_(n)=3230 g/mol), and polydimethylsiloxane (“PDMS”, M_(n)=1280 g/mol) macromonomers featuring an exo,exo-imide anchor group are prepared (FIG. 3). PS and PLA macromonomers of similar molar masses have been previously employed in the synthesis of well-defined bottlebrush polymers and are therefore attractive candidates for this example.⁹⁻¹⁰ For the diluents, we employ a family of racemic endo,exo-norbornenyl diesters (dimethyl (“DME”), diethyl (“DEE”), di-n-butyl (“DBE”), each with molar mass <300 g/mol) which may be easily assembled by Diels-Alder reactions of cyclopentadiene with the corresponding fumarate. We demonstrate different propagation rates for these norbornenyl diesters,²⁵ amenable to tuning the relative reactivity of diverse diluent/macromonomer pairs.

Homopolymerization kinetics. ROMP of each monomer in CH₂Cl₂ (0.05 M) is mediated by the highly active 3^(rd) generation olefin metathesis catalyst,²⁶ (H₂IMes)(pyr)₂(Cl)₂Ru═CHPh (“G3”, 0.5 mM). At different time points, aliquots are extracted from the reaction mixture and immediately quenched in a separate vial containing a large excess of ethyl vinyl ether. Subsequently, the quenched reactions are analyzed by size-exclusion chromatography (SEC) and ¹H NMR spectroscopy, allowing evaluation of the conversion, molar mass, and molar mass dispersity. As shown in FIG. 3, the depletion of monomers is first-order. Since the rate of initiation for G3 is much faster than that of propagation under these conditions²⁶⁻²⁷ the observed first-order rate constant (k_(obs)) can be used to calculate the second-order self-propagation rate constant (k_(homo)) according to Eq. 1 (M=monomer):

$\begin{matrix} {{- \frac{{d\lbrack M\rbrack}_{t}}{dt}} = {{k_{obs}\lbrack M\rbrack}_{t} = {{k_{homo}\left\lbrack {G\; 3} \right\rbrack}_{0}\lbrack M\rbrack}_{t}}} & (1) \end{matrix}$

The k_(homo), which is independent of the catalyst concentration, is of direct relevance to our copolymerization kinetic analyses (vide infra). The homopolymerization kinetic results are summarized in Table 1. Comparing the three macromonomers, PDMS possesses the largest k_(homo) of 21.6 M⁻¹ s⁻¹. The k_(homo) of PLA (17.2 M⁻¹ s⁻¹) is around four times as large as that measured for PS (4.18 M⁻¹ s⁻¹), in line with previous observations.^(23b) The k_(homo) values of the norbornenyl diesters trends inversely with the bulkiness of the ester substituents. Indeed, the k_(homo) measured for DME (18.7 M⁻¹ s⁻¹) is larger than that of DEE (14.6 M⁻¹ s⁻¹) or DBE (6.90 M⁻¹ s⁻¹). Collectively, these results show that the norbornene monomer sterics play an important role in the rate of ROMP.

TABLE 1 Homopolymerization reactions CH₂Cl₂ at 298K Expected Measured k_(homo) M_(n) ^(a) M_(n) ^(b) Monomer (M⁻¹ s⁻¹) (kg/mol) (kg/mol) Ð^(b) Conv. (%) PS 4.18 399 375 1.06  94^(c) PLA 17.2 323 319 1.01  99^(c) PDMS 21.6 128 131 1.02  99^(c) DME 18.7 21.0 21.7 1.02 100^(d) DEE 14.6 23.8 24.2 1.02 100^(d) DBE 6.90 29.4 29.6 1.02 100^(d) ^(a)Based on the monomer/G3 ratio of 100/1 ^(b)Determined by SEC light scattering detector. ^(c)Determined by SEC differential refractive index detector. ^(d)Determined by ¹H NMR.

Analytical methods for copolymerization kinetics. The homopolymerization kinetic analyses indicate that ROMP of each individual macromonomer or diluent is well-behaved. However, controlling side chain density and distribution also requires knowledge of the macromonomer/diluent copolymerization kinetics. To this end, we determine copolymerization reactions based on the Mayo-Lewis terminal model²⁸ (FIG. 4) in which the reactivity of two distinct propagating species (hereafter denoted as M₁* and M₂*) strictly depends on the monomer at the growing chain end. In other words, the chemical reactivity of the Ru catalyst is assumed to be primarily influenced by the electronic/steric properties of the latest formed alkylidene. The copolymerization of M₁ (macromonomer) and M₂ (diluent) can be described by four unique propagation reactions with individual rate constants k₁₁, k₁₂, k₂₁, and k₂₂. The reactivity ratios (r₁=k₁₁/k₁₂, r₂=k₂₂/k₂₁) are defined as the tendency for the propagating species to react with the same monomer over the other. As depicted in FIG. 4, the copolymerization is directed by the reactivity ratios, leading to sequences such as alternating, blocky, random, or gradient.

Historically, a number of methodologies have been established to determine the reactivity ratios for copolymerizations. Popular techniques include those pioneered by Mayo-Lewis,²⁸ Fineman-Ross,²⁹ and Kelen-Tüdös,³⁰ among others.³¹ While these linear regression methods bear irrefutable merit, they are derived from equations based on the steady-state approximation, with the assumption that the rates of crossover are identical; i.e., k₁₂[M₁*]_(t)[M₂]_(t)=k₂₁[M₂*]_(t)[M₁]_(t). As such, these prior methods are applicable under steady-state conditions in which the change in monomer feed is insignificant.³² Obtaining kinetic data in a low-conversion regime is analytically more challenging for fast polymerization reactions such as G3-mediated ROMP.

Given the aforementioned constraint, we develop another approach that bypasses the steady-state approximation. According to the terminal model, the time-dependent concentrations of M₁, M₂, M₁*, and M₂* can be described by the following ordinary differential equations:

$\begin{matrix} {{- \frac{{d\left\lbrack M_{1} \right\rbrack}_{t}}{dt}} = {{{k_{11}\left\lbrack M_{1}^{*} \right\rbrack}_{t}\left\lbrack M_{1} \right\rbrack}_{t} + {{k_{21}\left\lbrack M_{2}^{*} \right\rbrack}_{t}\left\lbrack M_{1} \right\rbrack}_{t}}} & (2) \\ {{- \frac{{d\left\lbrack M_{2} \right\rbrack}_{t}}{dt}} = {{{k_{12}\left\lbrack M_{1}^{*} \right\rbrack}_{t}\left\lbrack M_{2} \right\rbrack}_{t} + {{k_{22}\left\lbrack M_{2}^{*} \right\rbrack}_{t}\left\lbrack M_{2} \right\rbrack}_{t}}} & (3) \\ {{- \frac{{d\left\lbrack M_{1}^{*} \right\rbrack}_{t}}{dt}} = {{{k_{12}\left\lbrack M_{1}^{*} \right\rbrack}_{t}\left\lbrack M_{2} \right\rbrack}_{t} - {{k_{21}\left\lbrack M_{2}^{*} \right\rbrack}_{t}\left\lbrack M_{1} \right\rbrack}_{t}}} & (4) \\ {{- \frac{{d\left\lbrack M_{2}^{*} \right\rbrack}_{t}}{dt}} = {{{k_{21}\left\lbrack M_{2}^{*} \right\rbrack}_{t}\left\lbrack M_{1} \right\rbrack}_{t} - {{k_{12}\left\lbrack M_{1}^{*} \right\rbrack}_{t}\left\lbrack M_{2} \right\rbrack}_{t}}} & (5) \end{matrix}$

While the exact analytical solutions for Eqs. 2-5 cannot be obtained, numerical solutions for [M₁]_(t), [M₂]_(t), [M₁*]_(t), and [M₂*]_(t) can be generated if the propagation rate constants are provided. In this example, the homopolymerization rate constants k₁₁ and k₂₂ are independently measured (see Table 1). Further, the instantaneous monomer concentrations [M₁]_(t) and [M₂]_(t) during the copolymerization can be determined by the ethyl vinyl ether quenching method. In living ROMP, the sum of [M₁*]_(t) and [M₂*]_(t) should be [G3]₀. Taken collectively, the best numerical solutions for k₁₂ and k₂₁ for Eqs. 2-5 can be determined using a non-linear least-square curve fitting method (exemplary MATLAB codes provided below).

Copolymerization kinetics. We first determine the copolymerization of PS (0.05 M) and DME (0.05 M) mediated by G3 (0.5 mM) in CH₂Cl₂ (FIG. 5 top panel). The conditions, including the monomer and catalyst concentrations, are identical to those employed in homopolymerization reactions. Aliquots are extracted at different time points, quenched, and subjected to SEC and NMR analyses. The SEC traces indicated the continuing depletion of PS as well as the concomitant growth of the copolymer (FIG. 5, panel A). In addition, the instantaneous concentrations of both monomers can be determined by ¹H NMR integration of their distinct norbornenyl olefinic resonances. Plotting In([M]₀/[M]_(t)) as a function of time (FIG. 5, panel B) suggests that the decay of PS and DME approaches pseudo first order. However, we note that the first order kinetics are only strictly applicable in the event that both [M₁*]_(t) and [M₂*]_(t) are constant (see Eqs. 2 and 3). With the same G3 concentration of 0.5 mM, the propagation rates for PS and DME in the copolymerization reaction are, respectively, faster and slower than those measured independently in the homopolymerization reactions (FIG. 5, panel B). The increase in the rates of PS consumption in the copolymerization reaction can be attributed to cross-propagation being faster than self-propagation. Interestingly, an opposite trend is observed for DME.

To gain more insight, the kinetic profile of the copolymerization of PS and DME (1:1) is fitted to the terminal model using our analytical methods with known values of k_(PS-PS), k_(DME-DME), [PS]₀, [DME]₀, and [G3]₀ (FIG. 6A). The calculated curves of monomer conversion versus total conversion agree satisfactorily with the experimental data (FIG. 6B). This analysis determines k_(PS-DME) and k_(DME-PS) values of 7.74 and 13.2 M-¹ s⁻¹, respectively (Table 2, entry 1). The reactivity ratios (r_(PS)=0.54, r_(DME)=1.41) indicate gradient copolymerization and can be used in the simulation of instantaneous copolymer composition (vide infra). Copolymerizing PS and DME in a 1:1 feed ratio can therefore be expected to yield a polymer bearing 50% grafting density and a gradient distribution of PS side chains. In order to further examine the validity of our methods, the copolymerization of PS and DME in a 1:2 feed ratio is carried out and subjected to the same analyses (FIGS. 6C-6D), yielding comparable k_(PS-DME) and k_(DME-PS) values (Table 2, entry 2). As such, these experiments underline the ability of the terminal model to capture the copolymerization kinetics of G3-catalyzed ROMP.

TABLE 2 Copolymerization rate constants and reactivity ratios in CH₂Cl₂ at 298K [M₁]₀ [M₂]₀ k₁₁ k₁₂ ^(a) k₂₂ k₂₁ ^(a) Entry M₁ M₂ (M) (M) (M⁻¹ s⁻¹) (M⁻¹ s⁻¹) (M⁻¹ s⁻¹) (M⁻¹ s⁻¹) r₁ r₂ r₁r₂ 1 PS DME 0.050 0.050 4.18 7.74 18.7 13.2 0.54 1.41 0.76 2 PS DME 0.050 0.100 4.18 7.58 18.7 14.6 0.55 1.28 0.71 3 PS DEE 0.050 0.050 4.18 7.73 14.6 8.75 0.54 1.67 0.90 4 PS DBE 0.050 0.050 4.18 5.23 6.90 5.66 0.80 1.22 0.97 5 PS DBE 0.075 0.025 4.18 5.24 6.90 5.93 0.80 1.16 0.93 6 PLA DME 0.050 0.050 17.2 18.8 18.7 16.9 0.92 1.11 1.02 7 PLA DBE 0.050 0.050 17.2 16.7 6.90 7.95 1.03 0.87 0.90 8 PDMS DME 0.050 0.050 21.6 19.9 18.7 19.9 1.09 0.94 1.02 9 PDMS DBE 0.050 0.055 21.6 19.5 6.90 15.9 1.11 0.43 0.48 ^(a)Obtained from least-square curve fitting

We next determine the 1:1 copolymerization of PS and DEE (FIGS. 8A-8B). The measured k_(PS-DEE) (7.73 M⁻¹ s⁻¹, Table 2, entry 3) is very close to k_(PS-DME) (7.58-7.74 M⁻¹ s⁻¹), thus indicating similar chemical reactivity of the propagating species PS* (see FIG. 7) toward DME and DEE. In sharp contrast, k_(DEE-PS) (8.75 M⁻¹ s⁻¹) is notably smaller than k_(DME-PS) (13.2-14.6 M⁻¹ s⁻¹). This observation suggests that the PS* alkylidene steric/electronic effects are important in governing the rate of ROMP (perhaps more so than that of the approaching norbornenyl diester). The calculated reactivity ratios r_(PS) (0.54) and r_(DEE) (1.67) indicate gradient copolymerization. In addition, the r_(PS)×r_(DEE) product of 0.90 suggests an almost ideal copolymerization process in which each propagating species, PS* and DEE*, has the same preference for PS over DEE; i.e., k_(PS-PS)/k_(PS-DME)≈k_(DME-PS)/k_(DME-DME). The copolymerizations of PS and DBE in a 1:1 (FIGS. 8C-8D) and 3:1 (see FIGS. 19A and 19B) stoichiometry have also been examined. The propagation rate constants obtained from these experiments parallel each other (Table 2, entries 4, 5), again reflecting the competence of our analytical methods. The PS/DBE copolymerization is best described as near-ideal, approaching random, as evidenced by the reactivity ratios (r_(PS)=0.8, r_(DBE)=1.16-1.22) as well as their product (r_(PS)×r_(DBE)=0.93-0.97).

For studies and applications in which uniform grafting density is desired, the ability to access random copolymers is useful. The copolymerization reactions of PS with diluents imply that random copolymerization (r₁=r₂=1) may be achieved when both self-propagation rate constants are similar (k₁₁=k₂₂). To examine this, we turn our attention to the copolymerization of PLA (k_(homo)=17.2 M⁻¹ s⁻¹) and DME (k_(homo)=18.7 M⁻¹ s⁻¹). These experiments indicate that the decay of PLA is marginally slower than that of DME, in line with an almost random copolymerization process (FIGS. 8E-8F; Table 2, entry 6). Similarly, random copolymerization is observed for PLA/DBE (FIGS. 4G-4H; Table 2, entry 7) as well as PDMS/DME (FIGS. 41-4J; Table 2, entry 8). Lastly, gradient copolymers (Table 2, entry 9, r_(PDMS)=1.11, r_(DBE)=0.43) are obtained by copolymerization reaction of PDMS with DBE (FIGS. 4K-4L). The reactivity ratio product (r_(PDMS)×r_(DBE)=0.48) indicates a departure from ideal copolymerization. This observation appears to be correlated with the large differences in the self-propagation rate constants. Taken collectively, the copolymerization of a norbornene-functionalized macromonomer (PS, PLA, or PDMS) with a diluent (DME, DEE, or DBE) may generate either gradient or random copolymers. Kinetic analyses reveal similar k₁₂ values (PS=5.23-7.74 M⁻¹ s⁻¹, PLA=16.7-18.8 M⁻¹ s⁻¹, PDMS=19.5-19.9 M⁻¹ s⁻¹) and disparate k₂₁ values (PS=5.66-14.6 M⁻¹ s⁻¹, PLA=7.95-16.9 M⁻¹ s⁻¹, PDMS=15.9-19.9 M⁻¹ s⁻¹). This observation may attributed to the different steric, electronic, and ligating environments exerted by the pendent polymer group, linker, and anchor group (exo,exo-imide for macromonomer versus endo,exo-diester for diluent). The importance of the anchor group has been recently discussed by Matson in the context of self-propagation rates.³³

Instantaneous copolymer composition. From the copolymerization kinetics, the rate of monomer incorporation at any given time may be calculated according to Eqs. 2 and 3, allowing prediction of instantaneous copolymer composition as a function of total conversion. For example, copolymerizing PS and DME in a 1:1 feed ratio results in (PS-grad-DME)_(n) best described as a gradient graft polymer (FIG. 9A). Such a copolymer at 100% conversion possesses, on average, 50% grafting density; i.e., one polystyrene brush per two norbornene backbone repeat units. The difference in reactivity ratios leads to richer DME composition at early conversion and higher PS incorporation toward the end. We note that some gradient graft polymers have been previously accessed by grafting-from ATRP methods.³⁴ The brush distribution gradient is much less pronounced in copolymers (PLA-ran-DME)_(n) (FIG. 9B) and (PDMS-ran-DME)_(n) (FIG. 9C), in which the side chains are uniformly grafted across the entire polynorbornene backbone. Lastly, copolymerizing PDMS/DBE in a 1:1 ratio generates the gradient copolymer (PDMS-grad-DBE)_(n) (FIG. 9D). Unlike (PS-grad-DME)_(n), our simulations indicate that (PDMS-grad-DBE)_(n) is more densely grafted at early conversion. Coupled with sequential polymerization, copolymerizing PS/DME and PDMS/DBE may be exploited in the synthesis of normal tapered or inverse tapered block copolymers.³⁵

Synthesis of various grafting density polymers. To showcase the synthetic versatility of our methods, we preselect an array of polymers (PLA^(x)-ran-DME^(1-x))_(n) with various grafting densities (x=1.0, 0.75, 0.5, 0.25) and backbone lengths (n=167, 133, 100, 67, 33). These polymers may be easily prepared by mixing PLA, DME, and G3 in different ratios according to Eqs. 6 and 7 (M₁=macromonomer, M₂=diluent):

x=[M ₁]₀/([M ₁]₀+[M ₂]₀)  (6)

n=([M ₁]₀+[M ₂]₀)/[G3]₀  (7)

These copolymerization reactions are carried out under very mild conditions in CH₂Cl₂ (298 K, [G3]₀=0.5 mM, 15 min), and complete monomer consumption is verified by ¹H NMR spectroscopy. As shown in FIG. 10, the SEC analyses of the resulting polymers indicated low molar mass dispersities, or “polydispersity indices”, (Ð=1.01-1.03) as well as excellent agreement between the measured and targeted molar masses throughout the series (see also FIG. 17).

Reinforcing the NMR and SEC data, differential scanning calorimetry (DSC) provides further evidence supporting the controlled incorporation of both macromonomer and diluent (see FIG. 20). For example, DSC data collected for (PS^(0.5)-ran-DBE^(0.5))₂₀₀ shows one glass transition temperature (T_(g)) at 95° C., which lies between the T_(g) values of the pure components PS₁₀₀ (102° C.) and DBE₁₀₀ (71° C.). The presence of two T_(g)s would suggest either blocky copolymerization (rarely encountered) or microphase separation of PS-functionalized and DBE-functionalized segments. The observation of a single T_(g) instead supports random copolymerization as desired.

Conclusion: The current work introduces a general approach for simultaneously controlling the grafting density and side chain distribution of polymers. This method is achieved by ring-opening metathesis copolymerization of a norbornene-functionalized macromonomer (PS, PLA, or PDMS) with a discrete endo,exo-norbornenyl diester diluent (DME, DEE, or DBE). While such a system may appear at first glance untenable due to the vastly different steric profiles characteristic of the macromonomers and diluents, appropriate monomer design overcomes this challenge. By simple modifications to the diester substituents, the self-propagation rate constant (k_(homo)) of the diluents is adjusted to match or mismatch those of the norbornenyl macromonomers. To investigate the copolymerization kinetics, the reaction profiles are monitored and fitted to a terminal copolymerization model using a non-linear least-square curve fitting method. This analysis enables close inspection of previously unexplored reactivity ratios (r₁ and r₂) as well as cross-propagation rate constants (k₁₂ and k₂₁) for G3-catalyzed ROMP. In particular, we demonstrate that 1) copolymerizing a macromonomer/diluent pair with similar or dissimilar values of k_(homo) favors the generation of random (r₁≈r₂≈1) or gradient (r₁<1<r₂; r₁>1>r₂) copolymers, respectively; 2) different macromonomer/diluent feed ratios may be employed to vary the grafting density from 100% to 0%; and 3) the k₁₂ values measured for macromonomers (PS=5.23-7.74 M⁻¹ s⁻¹, PLA=16.7-18.8 M⁻¹ s⁻¹, PDMS=19.5-19.9 M⁻¹ s⁻¹) are very similar whereas the k₂₁ are substantially different (1=macromonomer, 2=diluent; see Table 2), reflecting the importance of the alkylidene ligands in metathesis rates. The determined reactivity ratios can be used to calculate the instantaneous copolymer composition, thus permitting visualizations of brush distributions. We further synthesize an array of monodisperse polymers (PLA^(x)-ran-DME^(1-x))_(n) with various preselected grafting densities (x=1.0, 0.75, 0.5, 0.25) and preselected backbone degrees of polymerization (n=167, 133, 100, 67, 33). These results demonstrate that ring-opening metathesis copolymerization can be exploited in the context of side chain density/distribution control. Simultaneous control over the density and distribution of grafts via grafting-through ROMP therefore expands the polymer synthetic toolbox, providing new opportunities for designing architecturally complex polymers spanning the linear-to-bottlebrush regimes.³⁶ We also contemplate the effects of grafting density variations on the self-assembly and rheological properties of graft polymers.

Experimental Conditions:

General considerations. Norbornene macromonomers PS⁹ and PLA¹⁰ are prepared according to the reported precedures. Norbornene diluents DME,³⁷ DEE,³⁸ and DBE³⁹ are prepared by Diels-Alder reactions according to the reported procedures. The second-generation ruthenium metathesis catalyst [(H₂IMes)(PCy₃)(Cl)₂Ru═CHPh] is generously provided by Materia, and G3 is prepared according to the reported precedure.²⁶ CH₂Cl₂ is dried by passing through an activated alumina column. Deuterated solvents are purchased from Cambridge Isotopes Laboratories, Inc. and used as received.

NMR, SEC, and DSC characterization. Ambient temperature NMR spectra are recorded on a Varian 300 MHz, 400 MHz, or 500 MHz NMR spectrometer. Chemical shifts (δ) are given in ppm and referenced against residual solvent signals (¹H, ¹³C). SEC data are collected using two Agilent PLgel MIXED-B 300×7.5 mm columns with 10 μm beads, connected to an Agilent 1260 Series pump, a Wyatt 18-angle DAWN HELEOS light scattering detector, and Optilab rEX differential refractive index detector. Online determination of dn/dc assumed 100% mass elution under the peak of interest. The mobile phase is THF. Thermal profiles of polymer samples are obtained using a Hitachi DSC7020 calorimeter with an aluminum reference pan. Following an initial run to erase thermal history (by heating from 25° C. to 130° C. at a rate of 10° C./min), sample temperature is maintained at 120° C. in an external oven while the furnace cooled for approximately 20 minutes. Samples are then removed from the oven, cooled for 45 seconds on a thermally conductive surface, then rerun through an identical calorimeter cycle (25-130° C., 10° C./min). The reported data are collected on the second heating ramp.

Synthesis of PDMS. A solution of N-(hexanoic acid)-cis-5-norbornene-exo-dicarboximide (6.00 g, 21.6 mmol), alcohol-terminated PDMS (18.1 g, 18.1 mmol, M_(n)=1000 g/mol, Gelest), EDC-HCl (5.52 g, 28.8 mmol), and DMAP (222 mg, 1.80 mmol) is prepared in 250 mL of dichloromethane. After stirring for 20 hours under air at room temperature, the organic solution is washed with 1 M HCl (3×75 mL), brine (3×75 mL), and deionized water (3×75 mL). The organic solution is stirred over anhydrous MgSO₄ then filtered, and volatile components are removed under vacuum. The product is filtered through a plug of silica with dichloromethane (2 L), and is dried in vacuo, affording PDMS as a colorless oil (18.6 g, 82%). ¹H NMR (CDCl₃, 300 MHz) δ 6.28 (s, 2H), 4.20 (dd, 4H), 3.61 (dd, 4H), 3.44 (dt, 10H), 3.27 (t, 4H), 2.33 (t, 2H), 1.59 (m, 9H), 1.31 (m, 6H), 1.21 (d, 1H), 0.88 (t, 4H), 0.52 (td, 4H), 0.07 (s, 104H). M_(n) (determined by ¹H NMR)=1280 g/mol.

Standard procedures for the determination of homopolymerization rate constants. A 4 mL vial is charged with a flea stir bar and a norbornene monomer (0.025 mmol) in CH₂Cl₂ at 298 K. While stirring vigorously, the polymerization is initiated by adding a CH₂Cl₂ solution of G3 (0.0125 M, 20 μL, 0.25 μmol) to achieve initial conditions of [norbornene]₀ (0.05 M) and [G3]₀ (0.5 mM). During the course of the reaction, aliquots (˜20-50 μL) are extracted at different time points and immediately quenched in a separate vial containing a large excess of ethyl vinyl ether (˜0.2 mL) in THF. The quenched reaction mixtures are subsequentially subjected to SEC and ¹H NMR analysis, allowing for the determination of [norbornene]_(t). For each homopolymerization experiment, the self-propagation rate constant k_(homo) is determined according to Eq. 1.

Standard procedures for the determination of copolymerization reactivity ratios. A 4 mL vial is charged with a flea stir bar and a CH₂Cl₂ solution of two norbornene monomers (M₁, M₂, each 0.025 mmol) at 298 K. While stirring vigorously, the copolymerization is initiated by adding a CH₂Cl₂ solution of G3 (0.0125 M, 20 μL, 0.25 μmol) to achieve initial conditions of [M₁]₀ (0.05 M), [M₂]₀ (0.05 M), and [G3]₀ (0.5 mM). During the course of the reaction, aliquots (˜20-50 μL) are extracted at different time points and immediately quenched in a separate vial containing a large excess of ethyl vinyl ether (˜0.2 mL) in THF. The quenched reaction mixtures are subsequentially subjected to SEC and ¹H NMR analysis, allowing for the determination of [M₁]_(t) and [M₂]_(t). Values of k₁₂ and k₂₁ are obtained by fitting the experimentally determined kinetic data to the numerical solutions for Eq. 2-5 using MATLAB non-linear least-square solver (Isqcurvefit) in conjunction with non-stiff differential equation solver (ode45).

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TABLE 3 Characterizations of graft polymers (PLAx-ran-DME1-x)n with various grafting densities (x = 1, 0.75, 0.5, 0.25) and backbone degrees of polymerization (n = 167, 133, 100, 67, 33) Difference Grafting Targeted between the density backbone DP Expected Measured expected and Molar mass (x) (n) M_(n) (kg/mol) M_(n) ^(a) (kg/mol) measured M_(n) dispersity (Ð^(a)) 100%  167 539 548 1.7% 1.025 133 431 432 0.1% 1.014 100 323 335 3.7% 1.008 67 216 227 5.3% 1.009 33 108 109 1.0% 1.017 75% 167 413 404 −2.2% 1.033 133 330 337 1.9% 1.029 100 248 250 0.8% 1.029 67 165 169 2.2% 1.019 33 82.6 81.1 −1.8% 1.023 50% 167 287 296 3.3% 1.026 133 230 234 1.7% 1.015 100 172 179 3.9% 1.010 67 115 119 3.4% 1.008 33 57.4 60.1 4.7% 1.019 25% 167 161 161 0.2% 1.009 133 129 126 −2.6% 1.014 100 96.6 97.4 0.8% 1.013 67 64.4 66.1 2.6% 1.014 33 32.2 32.3 0.2% 1.021 ^(a)As determined by SEC differential refractive index detector. The SEC analyses are performed on the ether vinyl ether quenched reaction mixtures without further workup or purification.

Instructions for Copolymerization Kinetics Fitting:

This model fits the copolymerization of two monomers (M₁ and M₂) with independently determined homopolymerization rate constants k₁₁ and k₂₂ (refer to the experimental section in the main text for details). The initial concentrations M₁C_(i) (M₁*, M₁ propagating species) and M₂C_(i) (M₂*, M₂ propagating species) are arbitrarily given as long as the sum of M₁C_(i) and M₂C_(i) equals C_(i) (G3 concentration). To use the codes,

-   -   1. Use MATLAB to save the following documents (see below)         FitKinData.m, odeSolver.m, and model.m, as .m files under the         same folder.     -   2. Use MATLAB to save the following array of kinetic data with         time (first column, unit: s), M₁(t) (second column, unit: M),         and M₂(t) (third column, unit: M). Note that the concentrations         at time zero are not included. To save the data as .mat file,         copy and paste the following example in the command window of         MATLAB (under the same folder):         -   KinDataTimePS_DBE31=[60.0000 0.0660 0.0210             -   120.0000 0.0566 0.0176             -   180.0000 0.0495 0.0150             -   240.0000 0.0435 0.0127             -   300.0000 0.0375 0.0109             -   420.0000 0.0289 0.0079             -   540.0000 0.0221 0.0056             -   720.0000 0.0150 0.0034];         -   save ExampleData     -   3. Open FitKinData.m file, follow comments line by line to setup         the .mat file name, the array name, k₁₁, k₂₂, initial         concentrations, as well as the boundary of the fitting         parameters for k₁₂ and k₂₁.     -   4. Run the FitKinData.m file to find solutions for k₁₂ and k₂₁.

MATLAB codes for copolymerization kinetics fitting FitKinData.m %This code is part of the SI of JACS 2017 by TPL, ABC, HYC, and RHG. close all %close all figure windows clc %clear command window clear all %clear all workspace load ExampleData %Load .mat file %KinDataTimePS_DBE31 is the array name containing data time, M1t, M2t data=KinDataTimePS_DBE31; %KinDataTimePS_DBE31_fit is fitting results containing [time M1t M2t M1C M2C] FittingResultName=‘KinDataTimePS_DBE31_fit’; %Self-propagation rate constants obtained from homopolymerization of M1 and M2 k11=4.18; %rate constant (M−1s−1) determined by homopolymerization of M1 k22=6.9; %rate constant (M−1s−1) determined by homopolymerization of M2 %Initial conditions for the copolymerization M1i=0.075; %initial concentration of M1 (M) M2i=0.025; %initial concentration of M2 (M) M1Ci=0.00025; %arbitrary initial concentration of M1C (M) M2Ci=0.00025; %arbitrary initial concentration of M1C (M). M1Ci+M2Ci = Ci %fitting parameters for k12 and k21: [LowerBound InitialValue UpperBound] k12=[0 5 20]; k21=[0 5 20]; %%%%%the following part should not be modified %%%%% Mi=[M1i M2i M1Ci M2Ci]; %save initial concentrations as Mi C=[k11 k22]; %save k11 and k22 as C %save Mi and C as constants.mat file in the current folder save(‘constants’,‘Mi’,‘C’) data=[0 M1i M2i;data]; %add initial M1 and M2 concentration to the data time=data(:,1); M1M2=data(:,2:3); P_lb=[k12(1) k21(1)]; P0 = [k12(2) k21(2)]; P_ub=[k12(3) k21(3)]; %fitting kinetic data with lsqcurvefit function. It will call odeSolver.m file %P0 = initial parameters for k12 and k21 %time = time points used to generate the analytical solution and the fit %M1M2 = Experimentally determined M1 and M2 concentrations at different time points %P_result = [k12 k21] from the best fit [P_result,resnorm] = lsqcurvefit(@odeSolver,P0,time,M1M2,P_lb,P_ub); %use the k12 and k21 obtained from the best fit to simulate the reaction profile odeSolver(P_result, [0 time(end)*1.3]); load AllResult %load the reaction profile generated by odeSolver code eval([FittingResultName ‘= [time_ode Y];’]); r1Mr2=k11*k22/P_result(1)/P_result(2); %calculate r1 x r2 plot(data(:,1),data(:,2),‘.b’,data(:,1),data(:,3),‘.r’,‘markers’,12) hold plot(time_ode,Y(:,1),‘b’,time_ode,Y(:,2),‘r’,time_ode,Y(:,3),‘m’,time_ode,Y(: ,4),‘k’) %set legends, x-, y-label, x-axis limit. Report fitting parameters legend(‘M_1 exp’,‘M_2 exp’,‘M_1 fit’,‘M_2 fit’,‘M_1* fit’,‘M_2* fit’) xlabel(‘Time (s)’) ylabel(‘[M](t) (M)’) xlim([0 time(end)*1.3]) title({strjoin({‘k_1_1 = ‘,num2str(k11),’ M{circumflex over ( )}−{circumflex over ( )}1s{circumflex over ( )}−{circumflex over ( )}1, k_2_2 = ‘,num2str(k22),’ M{circumflex over ( )}−{circumflex over ( )}1s{circumflex over ( )}−{circumflex over ( )}1’}),... strjoin({‘k_1_2 = ’,num2str(P_result(1),‘%.2f’),’ M{circumflex over ( )}−{circumflex over ( )}1s{circumflex over ( )}−{circumflex over ( )}1, k_2_1 = ‘,num2str(P_result(2),‘%.2f’),‘ M{circumflex over ( )}−{circumflex over ( )}1s{circumflex over ( )}−{circumflex over ( )}1’}),... strjoin({‘r_1 = ’ ,num2str(k11/P_result(1),‘%.2f’),’, r_2 = ‘,num2str(k22/P_result(2),‘%.2f’),’, r_1\timesr_2 = ‘,num2str(r1Mr2,‘%.2f’)}),... ‘TPL, RHG, JACS 2017’}) hold off clear k11 k12 k21 k22 M1Ci M1i M1M2 M2Ci M2i Mi P0 P_lb P_ub r1Mr2 resnorm time C P_result data ans FittingResultName time_ode Y odeSolver.m %This code is part of the SI of JACS 2017 by TPL, ABC, HYC, and RHG. function y = odeSolver(k, time) load constants [t,Y]=ode45(@(t,Y) model(t,Y,k), time, Mi); y=Y(:,1:2); time_ode=t; save(‘AllResult’,‘Y’,‘time_ode’) model.m %This code is part of the SI of JACS 2017 by TPL, ABC, HYC, and RHG. function dMdt = model(t,M,k) load constants M1=M(1); M2=M(2); M1C=M(3); M2C=M(4); k11=C(1); k22=C(2); k12=k(1); k21=k(2); dM1dt = −k11 * M1C * M1 − k21 * M2C * M1; dM2dt = −k22 * M2C * M2 − k12 * M1C * M2; dM1Cdt = k21 * M2C * M1 −k12 * M1C * M2; dM2Cdt = −k21 * M2C * M1 + k12 * M1C * M2; dMdt = [dM1dt; dM2dt; dM1Cdt; dM2Cdt];

Example 2A: Design, Synthesis, and Self-Assembly of Polymers with Tailored Graft Distributions

Abstract: Grafting density and graft distribution impact the chain dimensions and physical properties of polymers. However, achieving precise control over these structural parameters represents long-standing synthetic challenges. In this example, we provide a versatile strategy to synthesize polymers with tailored architectures via a grafting-through ring-opening metathesis polymerization (ROMP). One-pot copolymerization of an ω-norbornenyl macromonomer and a discrete norbornenyl co-monomer (diluent) provides opportunities to control the backbone sequence and therefore the side chain distribution. Toward sequence control, the homopolymerization kinetics of 23 diluents are studied, representing diverse variations in the stereochemistry, anchor groups, and substituents. These modifications tune the homopolymerization rate constants over at least two orders of magnitude (0.36 M⁻¹ s⁻¹<k_(homo)<82 M⁻¹ s⁻¹). Rate trends are identified and elucidated by complementary mechanistic and density functional theory (DFT) studies. Building on this foundation, complex architectures are achieved through copolymerizations of selected diluents with a poly(D,L-lactide) (PLA), polydimethylsiloxane (PDMS), or polystyrene (PS) macromonomer. The cross-propagation rate constants are obtained by non-linear least squares fitting of the instantaneous co-monomer concentrations according to the Mayo-Lewis terminal model. In-depth kinetic analyses indicate a wide range of accessible macromonomer/diluent reactivity ratios (0.08<r₁/r₂<20), corresponding to blocky, gradient, or random backbone sequences. We further demonstrate the versatility of this copolymerization approach by synthesizing AB graft diblock polymers with tapered, uniform, and inverse-tapered molecular “shapes.” Small-angle X-ray scattering analysis of the self-assembled structures illustrates effects of the graft distribution on the domain spacing and backbone conformation. Collectively, the insights provided herein into a ROMP mechanism, monomer design, and homo- and copolymerization rate trends offer a general strategy for the design and synthesis of graft polymers with arbitrary architectures. Controlled copolymerization therefore expands the parameter space for molecular and materials design.

Introduction: Molecular architecture impacts the chemical and physical properties of all polymers. Achieving precise control over the chain connectivity, sequence, and symmetry presents synthetic challenges as well as rich opportunities for materials design. Over the past several decades, advances in polymerization have enabled the synthesis of polymers with complex architectures.¹⁻⁴ Graft polymers are a class of such nonlinear architectures featuring polymeric side chains attached to a polymeric backbone. The grafting density and distribution of grafts along the backbone influence the steric interactions between side chains and in turn influence the physical properties. Graft polymers display many unique properties compared to their linear analogues, such as extended chain conformations,⁵⁻⁸ increased entanglement molecular weights,⁹⁻¹² and architecture-dependent rheological behavior.¹³⁻¹⁶ Recent studies have harnessed these properties in a wide variety of applications in photonics,¹⁷⁻¹⁹ drug delivery,²⁰⁻²² transport,²³⁻²⁴ and thermoplastics.²⁵⁻²⁶ Continued progress in synthetic command over polymer architecture enables further studies of structure-property relationships and inspires new potential applications.

Graft polymers represent ideal platforms to study how chain connectivity defines nanostructures and thereby physical properties. Despite the importance of grafting density and graft distribution, prior synthetic strategies that permit precise and preselected control of these parameters have been currently limited. Grafting-to²⁷⁻³⁰ and grafting-from³¹⁻³⁴ approaches require multiple steps in which side chains are either attached to or grown from a pre-formed backbone. Steric congestion along the backbone typically prevents precise control over the molecular weight, grafting density, and side chain distribution. As a result, the synthesis of well-defined architectural variants—let alone materials with variable chemical compositions—is challenging. Grafting-through ring-opening metathesis polymerization (ROMP) closes this gap by affording wide functional group tolerance and enabling simultaneous control over side chain and backbone lengths.³⁵⁻³⁷ In another example demonstrate a ROMP-type strategy that provides access to polymers with uniform grafting densities spanning the linear to bottlebrush regimes.³⁸ In this example, we further expand the scope of architectural design by demonstrating that methods of the present invention can be exploited to further tune “molecular shapes.”

Our approach employs controlled copolymerization of a macromonomer and a small-molecule diluent. The relative reactivity of the two co-monomers directly dictates the spatial arrangement of the side chains. For example, if the macromonomer and diluent copolymerize at approximately the same rate, the side chains are therefore uniformly distributed along the polymer backbone (FIG. 22A). Such polymers are widely termed “cylindrical molecular brushes” due to their steric-induced stiffness and axes of symmetry.³⁹⁻⁴³ These cylindrical brushes can be modeled as wormlike chains with the same average cross-sectional radius (R_(c)) along the entire backbone.^(5,44-46) On the other hand, if the macromonomer and diluent copolymerize at different rates, the resulting gradient sequences may template different side chain conformations. Depending on the extent of side chain stretching, R_(c) varies and tapered, non-cylindrical molecular shapes result (FIG. 22B). Control over the co-monomer distribution therefore opens opportunities to manipulate the chain dimensions and physical properties.

In this example, we provide the demonstration that varying the stereochemistry and steric profiles of discrete co-monomers enables the synthesis of well-defined graft polymers with tunable grafting density and graft distribution. We first discuss the homopolymerization kinetics of a library of discrete norbornenyl monomers, then build complexity through controlled copolymerizations of these small molecules with ω-norbornenyl macromonomers. Trends in the homo- and cross-propagation rates are outlined to provide guidance for future rational design of polymer architectures with arbitrary graft chemistry and distribution. We illustrate the versatility of this copolymerization strategy through the synthesis of graft polymers with different anticipated molecular shapes. The physical consequences of varying the graft distribution are discussed in the context of block polymer self-assembly.

Monomer Design. Previous work introduced endo,exo-norbornenyl dialkylesters as appropriate discrete monomers (diluents) to control the grafting density of polymers with poly(D,L-lactide) (PLA, M_(n)=3230 g mol⁻¹), polydimethylsiloxane (PDMS, M_(n)=1280 g mol⁻¹), or polystyrene (PS, M_(n)=3990 g mol⁻¹) side chains.³⁸ Across all macromonomer/diluent combinations and feed ratios, kinetic analyses indicated approximately equal rates of co-monomer consumption and therefore approximately uniform side chain distributions. Obtaining non-uniform side chain distributions requires changing the relative reactivity of the macromonomer and diluent. We show that designing new small-molecule co-monomers is a convenient route. This strategy avoids tedious end-group modifications to the macromonomers and retains the synthetic utility of one-pot batch copolymerization. Semi-batch methods (involving continuous addition of one monomer to another)⁴⁷⁻⁴⁸ require additional instrumentation and optimization of factors such as feed ratio and feed rate.⁴⁹⁻⁵⁰ Similarly, while sequential addition of macromonomers with different molecular weights can also provide access to tapered architectures,⁵¹ such approach requires the preparation of multiple well-defined macromonomers and fixes the grafting density at 100%.

FIG. 23 highlights a strategy for monomer design. Species 1a-1j, 2a-2d, 3a-3d, 4a-4c, and 5a-5c are summarized in FIG. 23. The polymerizable strained olefin, anchor group, and substituents can all be readily modified. Substituted norbornenes are selected for this example due to (1) the ease of modifying the stereochemistry and functional groups and (2) the high ring strain, which disfavors unproductive [2+2]cycloreversion.⁵² The importance of the anchor group in homopolymerization kinetics has been demonstrated for both discrete norbornenes⁵³⁻⁵⁴ and more recently, ω-norbornenyl macromonomers.⁵⁵ In contrast, anchor group effects on the copolymerization of discrete monomers and macromonomers have not been previously studied. In order to investigate these effects, discrete substituted norbornenes with five different types of anchor groups are synthesized: endo,exo-diester (dx-DE, “1”), endo,endo-diester (dd-DE, “2”), exo,exo-diester (xx-DE, “3”), endo-imide (d-l, “4”), and exo-imide (x-l, “5”). For each anchor group, monomers with different substituents (R) are prepared, including for example homologous alkyl groups or para-substituted phenyl rings. All monomers can be prepared in high yields in one or two steps from commercially available starting materials. (Further synthetic details can be found in the Supporting Information.) These steric and electronic variations provide a diverse library of co-monomers for ROMP.

The homopolymerization kinetics of all monomers are studied under the same conditions. ROMP of each monomer in dichloromethane ([M]=50 mM) is catalyzed by the fast-initiating third-generation ruthenium metathesis catalyst, (H₂IMes)(pyr)₂(Cl)₂Ru═CHPh ([G3]₀=0.5 mM). Over the course of the polymerization, aliquots (<20 μL) are collected and immediately quenched into separate vials containing excess ethyl vinyl ether and a silica-bound metal scavenger (SiliaMetS).⁵⁶ Removing the quenched ruthenium complex from solution prevents potential reactivation and undesired metathesis that would affect the apparent rates. Analysis by size-exclusion chromatography (SEC) and ¹H NMR spectroscopy indicates first-order rate dependence on monomer concentration. The first- and second-order rate constants (k_(obs) and k_(homo), respectively) are determined according to Eq. 1:

$\begin{matrix} {{- \frac{{d\lbrack M\rbrack}_{t}}{dt}} = {{k_{obs}\lbrack M\rbrack}_{t} = {{k_{homo}\left\lbrack {G\; 3} \right\rbrack}_{0}\lbrack M\rbrack}_{t}}} & (1) \end{matrix}$

For many monomers, the rate constants are determined at least in triplicate. The calculated values typically varied by no more than five percent (FIGS. 49A-49B).

Studying trends in k_(homo) with variations in steric and electronic structure guides monomer design. The first class of monomers demonstrated herein features endo,exo-diester anchor groups (dx-DE). The homopolymerization kinetics of ten dx-DE monomers with different substituents are analyzed (1a-1j, FIGS. 23 and 24). The monomers are readily synthesized by esterification of commercially available norbornene endo,exo-dicarboxylic acid with the appropriate alcohol (1a-d, Scheme 1). (For the synthesis of 1e-1j, FIGS. 23 and 24, the acyl chloride derivatives are used, Scheme 2.) In a series of monomers with homologous alkyl substituents (R=methyl, ethyl, n-propyl, n-butyl; 1a-d, FIGS. 23 and 24), k_(homo) decreases with increasing substituent size. Increasing the steric bulk with isopropyl- and tert-butyl-substituted monomers (1e-f, FIGS. 23 and 24) further decreases k_(homo). These results indicate that sterics clearly impact the homopolymerization kinetics: for example, the methyl-substituted monomer polymerizes over three times faster than the tert-butyl-substituted analogue (k_(homo)=18.7 versus 5.36 M⁻¹ s⁻¹). The effects of electronic variations are also determined. Monomers with ethyl (1b, 14.6 M⁻¹ s⁻¹) and trifluoroethyl (1g, 10.5 M⁻¹ s⁻¹) substituents polymerize at approximately the same rate. Comparison of dx-DE monomers with different para-substituted phenyl rings further reveals that the electronic effects are minor. dx-norbornenyl diphenylester (1h) has a larger k_(homo) (8.36 M⁻¹ s⁻¹) than monomers with either an electron-withdrawing para-trifluoromethyl group (ii, 5.14 M⁻¹ s⁻¹) or an electron-donating para-methoxy group (1j, 7.76 M⁻¹ s⁻¹). These electronic variations may exist too far away from the polymerizable olefin to affect k_(homo). Modifying norbornene itself rather than the distal substituents (for example, by substituting oxanorbornene or otherwise changing the bridge position) may result in more apparent electronic effects.

Changing the stereochemistry of the diester anchor groups further demonstrates the effects of steric variations on polymerization rates. (Synthetic details: Schemes 3-4.) Comparing series with the same substituents (FIG. 25A) indicates that dx-DE monomers (1a-d) all polymerize significantly faster than the corresponding endo,endo isomers (dd-DE, 2a-d) and slightly slower than the corresponding exo,exo isomers (xx-DE, 3a-d). For example, the measured k_(homo) for dx-norbornenyl dimethylester is 18.7 M⁻¹ s⁻¹, while k_(homo) values for the dd-DE and xx-DE analogues are 2.24 M⁻¹ s⁻¹ and 30.8 M⁻¹ s⁻¹, respectively. The same anchor group trend occurs for ethyl-, n-propyl-, and n-butyl-substituted norbornenyl diesters and is anticipated to be independent of the substituent.

In order to further examine the relationship between anchor groups and homopolymerization kinetics, norbornenyl monomers with endo-imide (d-l) and exo-imide (x-l) linkages are also synthesized (Schemes 5-6). The x-l anchor group has been widely incorporated in macromonomers toward the synthesis of bottlebrush polymers by grafting-through ROMP,^(21,55,57-59) motivating our interest in imide-based diluents. Compared to diester anchor groups, imides are more rigid due to their fused rings and thereby change the monomer steric profile. The electronic character differs as well, since the electron density of an imide oxygen is typically greater than the electron density of an ester oxygen. The interplay of steric and electronic influences are discussed further in the following section.

FIG. 25B compares k_(homo) for monomers with each of the five anchor groups. The endo/exo rate difference between d-l and x-l is magnified compared to the endo/exo rate differences observed among the diester-substituted monomers. The k_(homo) values for methyl-substituted dd-DE and xx-DE are 2.24 and 30.8 M⁻¹ s⁻¹ respectively, representing a tenfold rate difference; in comparison, the k_(homo) values for methyl-substituted d-l and x-l are 0.814 and 82.4 M⁻¹ s⁻¹ respectively, representing a hundredfold rate difference. FIG. 25B also shows that the steric effects of the R group are smaller for x-l and d-l compared to the diester series. For monomers containing the same substituents, the following trend in k_(homo) is observed: d-l<dd-DE<dx-DE<xx-DE<x-l.

FIG. 26 and Table 4 summarize the homopolymerization kinetics for all monomers studied herein. Variations in the anchor groups and substituents afford a wide range of k_(homo) over two orders of magnitude, spanning 0.362 M⁻¹ s⁻¹ (2d) to 82.4 M⁻¹ s⁻¹ (5a). This library of monomers can be readily diversified by simple esterification reactions, providing a versatile platform for tuning the polymerization rates. Understanding the origin of trends in k_(homo) provides insight into the ROMP mechanism. While developing a complete mechanistic understanding is outside the scope of this study, we aim to identify key components of k_(homo) in order to facilitate applications of this method as well as future monomer design.

Origin of Rate Trends. Polymerization rates are determined by a combination of steric and electronic factors. Our results show that steric effects dominate: (1) In a series of monomers with homologous alkyl R groups, the electronic character is similar but k_(homo) decreases as the steric bulk increases (FIG. 24). (2) k_(homo) is relatively insensitive to distal electronic variations (for example, via para-substitution of phenyl R groups, FIG. 24). (3) k_(homo) decreases for endo-substituted monomers compared to the corresponding exo isomers (FIGS. 25A-25B). In agreement with this work, previous studies of the ROMP of norbornene derivatives have also observed that endo isomers polymerize more slowly than their exo counterparts.^(54,60-63)

The observed rate trends may be motivated by a combination of factors, including but not limited to pyridine coordination, olefin coordination, cycloaddition, and formation of a six-membered chelate involving the ruthenium center and the ester- or imide-functionalized chain end.⁶⁴ In order to deconvolute these potential contributions to k_(homo), we examined the mechanism of ROMP. Based on reported results for related phosphine-based catalysts,⁶⁵⁻⁶⁷ we contemplate a dissociative pathway (FIG. 27A) in which pyridine dissociation (K_(eq,1)=k₁/k⁻¹, K_(eq,2)=k₂/k⁻²) generates a 14-electron intermediate (b) that can coordinate with a free olefin (c, K_(eq,3)=k₃/k⁻³). The olefin adduct then undergoes cycloaddition (k₄) to form a metallacyclobutane intermediate. Subsequent cycloreversion yields a P_(n+1) alkylidene and regenerates the 14-electron species. From a Van't Hoff analysis, Guironnet and coworkers recently reported an equilibrium constant K_(eq,1)=k₁/k⁻¹=0.5 M in CD₂Cl₂ at 298 K.⁶⁸ In agreement with this work, we observe a similar K_(eq,1) value from ¹H NMR pyridine titration experiments (0.25 M, FIG. 50). The large K_(eq,1) value indicates that >99.8% of the precatalyst G3 exists as the monopyridine adduct in solution under the conditions employed in our homo- and copolymerization studies ([G3]₀=0.5 mM). As a result, the concentration of free pyridine is approximately equal to the initial concentration of G3 (i.e., [pyr]≈[G3]₀). We derive a simplified rate expression corresponding to a proposed dissociative ROMP pathway in which olefin coordination is the rate-limiting step:⁶⁹

$\begin{matrix} {{- \frac{{d\lbrack M\rbrack}_{t}}{dt}} = {{{k_{homo}\left\lbrack {G\; 3} \right\rbrack}_{0}\lbrack M\rbrack}_{t} \approx {{\frac{K_{{eq},2}k_{3}}{K_{{eq},2} + \lbrack{pyr}\rbrack}\left\lbrack {G\; 3} \right\rbrack}_{0}\lbrack M\rbrack}_{t}}} & (2) \end{matrix}$

In this rate expression, K_(eq,2) corresponds to dissociation of the second pyridine and is affected by the identity of the alkylidene ligand. At high catalyst concentrations ([pyr]>>K_(eq,2)), a pseudo-zeroth-order dependence on [G3]₀ is observed.⁶⁸ At low catalyst concentrations however, we observe a rate dependence on [G3]₀ for monomers 5a and 5b (FIG. 51). Collectively, these kinetic analyses are consistent with a dissociative pathway.⁷⁰

Density functional theory (DFT) methods are employed to address potential chelation effects. Chelation sequesters the catalyst in an unproductive form (FIG. 27A, a) and therefore slows the polymerization rate.⁷¹ For methyl-substituted endo,endo- and exo,exo-norbornenyl diesters (2a and 3a, respectively), the ground-state potential energy surfaces corresponding to one productive ROMP cycle are computed (FIGS. 27B and 52A-52B). The relative free energies at 298 K (ΔG) indicate that formation of the six-membered chelate is more favorable for the endo isomer (ΔΔG_(chelate)=9.64 kcal mol⁻¹) than for the exo isomer (ΔΔG_(chelate)=5.87 kcal mol⁻¹). The calculated free energies corresponding to olefin coordination to the vacant species, ΔΔG_(binding), are similar for the endo and exo isomers (8.86 and 8.91 kcal mol⁻¹, respectively). These results indicate that disruption of chelation by olefin binding should be more favorable for exo isomers than endo isomers (by 3.72 kcal mol-1). This disparity provides a possible reason for the observed endo/exo rate differences (k_(homo)=30.8 M⁻¹ s⁻¹ for 3a, 2.24 M⁻¹ s⁻¹ for 2a). These results are consistent with previous reports on the ROMP of discrete norbornenyl monomers with similar ruthenium catalysts^(64,66,72) and are contemplated to be valid whether olefin coordination (k₃<<k₄) or cycloaddition (k₃>>k₄) is the rate-limiting step.⁷³ Insights into the rate trends from mechanistic studies help identify important elements of monomer design and, therefore, opportunities for controlled copolymerization.

Copolymerization Kinetics. In order to analyze the copolymerization kinetics of a macromonomer and a discrete co-monomer, the Mayo-Lewis terminal model is adapted for G3-catalyzed ROMP.³⁸ The terminal model assumes that, for a mixture of two monomers M₁ and M₂, there are two propagating species (M₁* and M₂*) whose reactivities solely depend on the last-incorporated monomer.⁷⁴ The copolymerization kinetics can be captured by four propagation reactions involving M₁* and M₂*, each described by a unique rate constant k. FIG. 28 shows the relevant reactions for a mixture of a discrete diluent (M₂) and a macromonomer (M₁): (A) diluent self-propagation (M₂*→M₂*, k₂₂), (B) cross-propagation via addition of M₁ to M₂* (M₂*→M₁*, k₂₁), (C) macromonomer self-propagation (M₁*→M₁*, k₁₁), and (D) cross-propagation via addition of M₂ to M₁* (M₁*→M₂*, k₁₂). The conversion over time of all species can be described by a system of four ordinary differential equations. Non-linear least squares regression, described in a previous report,³⁸ is used to fit the instantaneous monomer concentrations over the entire course of the copolymerization. Finding the best numerical solutions for the cross-propagation rates k₁₂ and k₂₁ enables determination of the reactivity ratios, r₁=k₁₁/k₁₂ and r₂=k₂₂/k₂₁.

The relative reactivity, captured by r₁ and r₂, determines the polymer sequence. r₁ and r₂ can be tuned by building on insights into homopolymerization rate trends. Monomer design ultimately enables architecture design: for a polymerizable macromonomer with any side chain chemistry, a discrete co-monomer can be selected among those in FIG. 26 or otherwise designed to target preselected backbone sequences. In turn, control over the backbone sequence directly controls side chain distribution. We first discuss general trends and opportunities for copolymerization, then outline potential implications for polymer architectures by design.

In order to study the impact of monomer structure on the copolymerization kinetics, we select 13 diluents and copolymerized each with the same co-norbornenyl macromonomer (PLA, M_(n)=3230 g mol⁻¹) (FIG. 29A). FIG. 29B arranges these discrete co-monomers in order of increasing k₂₂. For all copolymerization experiments, the total backbone degree of polymerization (N_(bb)) and monomer feed ratio (f) are fixed: given x equivalents of the diluent and y equivalents of PLA relative to 1 equivalent of G3, N_(bb)=x+y≈200 and f=x/y≈1. The copolymerization conditions, including monomer and catalyst concentrations, are identical to those for the homopolymerization experiments described above: [M₁]₀=[M₂]₀=50 mM, [G3]₀=0.5 mM.⁷⁵ The kinetics are monitored in the same way as the homopolymerization kinetics, i.e., by quenching aliquots of the polymerization mixture. The instantaneous concentrations of the macromonomer and diluent are determined by integrating the olefin resonances in ¹H NMR spectra, and k₁₂ and k₂₁ are obtained by non-linear least squares regression. SEC data for all copolymers indicate low dispersities (

<1.1) and similar molecular weights (FIG. 53, Table 5).

FIG. 29C shows the self-propagation rate constants (k₁₁, k₂₂) and reactivity ratios (r₁, r₂) for the copolymerization of PLA (M₁) with different diluents (M₂). (All data, including the cross-propagation rate constants k₁₂ and k₂₁, are compiled in Table 6.) k₁₁ is constant throughout the series (=17.2 M⁻¹ s⁻¹) since M₁ is the same in each co-monomer pair, while k₂₂ varies over a wide range due to anchor group and substituent effects (2d: 0.362 M⁻¹ s⁻¹ to 5a: 82.4 M⁻¹ s⁻¹). As k₂₂ increases, r₂ also increases. The magnitude of r₂ reflects the reactivity of the propagating alkylidene M₂* toward free M₁ and M₂.⁷⁶ In the case that r₂<1, for example when PLA is copolymerized with dd-DE or d-l diluents (2d to 2a, 0.4<r₂<0.9), M₂* preferentially adds M₁. In the opposite case r₂>1, for example when PLA is copolymerized with dx-DE, xx-DE, or x-l diluents (3d to 5a, 1.2<r₂<3.1), M₂* preferentially adds M₂ instead. In other words, if a diluent is the terminal unit of the propagating species, the probability of incorporating either a macromonomer or another diluent reflects the difference between the homopolymerization rate constants: when k₂₂<k₁₁, r₂<1 and M₂* favors macromonomer addition; on the other hand, when k₂₂>k₁₁, r₂>1 and M₂* favors diluent addition.⁷⁷ Translating these trends to the copolymer sequence also requires examination of r₁, which reflects consumption of the other propagating species M₁*. FIG. 29C shows that, as k₂₂ increases, r₁ generally decreases, opposite the trend observed for r₂. These observations suggest that both M₁* and M₂* (1) favor incorporating M₂ when k₂₂≳k₁₁ and (2) favor incorporating M₁ when k₂₂<k₁₁. In other words, both cross-propagation terms (k₁₂ and k₂i) are functions of the incoming olefin (to first order) and appear relatively insensitive to the nature of the pendant chain.

We note that, while r₁ generally decreases with increasing k₂₂, the trend is not monotonic. These results highlight the additional complexity that copolymerization introduces. While informative, the difference between the homopolymerization rate constants (k₁₁−k₂₂) is not a universal predictor for the values of r₁ and r₂ (nor therefore the copolymer sequence). For example, when PLA is copolymerized with a xx-DE diluent, r₂ varies but r₁ remains the same (=0.36±0.02), regardless of whether k₂₂<k₁₁ (3d, 3c, and 3b) or k₂₂>k₁₁ (3a). Meanwhile, when PLA is copolymerized with the dx-DE analogue of 3a (i.e., 1a), the self-propagation rates are equal (k₂₂=k₁₁) and both r₁ and r₂ are approximately equal to 1. These observations suggest that the key interactions identified in this example of diluent homopolymerization rate trends do not fully capture the relative reactivity upon copolymerization. The individual second-order rate constants (k₁₁, k₁₂, k₂₁, k₂₂) are affected by both (1) pyridine binding (K_(eq,2)) and (2) chelation and olefin binding (k₃). Both those terms are dictated by the identities of the approaching olefin monomer and the propagating alkylidene. We note that the large disparity between the molecular weights of the PLA macromonomer and diluents (10- to 20-fold) may play a significant role in the departure from simple chain-end control. Under the copolymerization conditions (rapid stirring in dilute solution), simple diffusion of free monomers to the catalyst active site may not be expected to limit propagation. However, beyond the anchor group and substituent effects outlined for discrete diluents, the presence of polymeric side chains in proximity to the metal center should amplify steric congestion. Excluded volume interactions and solvent quality may further affect the steric and electronic environment around the propagating metal center.

Graft Polymer Architecture. Monitoring the copolymerization kinetics enables determination of the instantaneous composition and therefore the graft polymer architecture. Using the experimentally determined rate constants, the probability of incorporating either a diluent or a macromonomer at any point in the growing chain can be simulated.³⁸ FIGS. 30A-30C plot these probabilities as a function of the total conversion for several PLA/diluent pairs. If r₁>r₂, gradient sequences are obtained. The copolymers are rich in M₁ at early conversions and rich in M₂ at later conversions, producing tapered side chain distributions (e.g., PLA+4a, FIG. 30A). If r₁≈r₂≈1, the copolymer backbone sequence is approximately random and therefore the side chains are uniformly distributed (e.g. PLA+1a, FIG. 30B). Lastly, if r₁<r₂, the inverse-tapered graft polymers are obtained, which are rich in M₂ at early conversions and rich in M₁ at later conversions (e.g., PLA+5a, FIG. 30C).

The copolymerization methods outlined herein provide a general approach to architecture design for any side chain chemistry. In principle, given any polymerizable macromonomer, a diluent may be designed to access any desired sequence. Although the magnitudes of r₁ and r₂ are presently determined de novo, insights into the relationships among r₁, r₂, and diluent structure should guide the selection of appropriate macromonomer/diluent pairs. In order to further illustrate these design principles, the copolymerization kinetics of various diluents with either a PDMS (M_(n)=1280 g mol⁻¹) or PS (M_(n)=3990 g mol⁻¹) macromonomer are also studied here. PDMS and PS polymerize faster (k₁₁=21.6 M⁻¹ s⁻¹) and slower (k₁₁=4.18 M⁻¹ s⁻¹) than PLA, respectively. The selected diluents all homopolymerize slower than PDMS (k₂₂<k₁₁, with the exception of 3a) and faster than PS (k₂₂>k₁₁). The self-propagation rate constants and reactivity ratios are provided in FIG. 31. All values are compiled in Tables 7-8, and SEC data are provided in FIGS. 54-55 and Tables 9-10.

Copolymerizations of PDMS with each of the selected diluents generally follow the same trends outlined for PLA/diluent copolymerizations. As k₂₂ increases while k₁₁ remains constant, r₂ increases and r₁ decreases. In other words, as k₂₂ increases, both M₁* and M₂* increasingly favor incorporating M₂ instead of M₁. The xx-DE diluents (3a, 3d) are again outliers, leading to smaller values of r₁ than diluents with any other anchor group. As a result, at least for copolymerizations with PDMS or PLA macromonomers, the xx-DE anchor group favors gradient sequences that are M₂-rich at early conversions and M₁-rich at later conversions. Copolymerizations of PS with any of the selected diluents reveal a similar kinetic preference for gradient sequences. Unlike copolymerizations with either PLA or PDMS, regardless of the relative magnitude of k₂₂ (2.7<k₂₂−k₁₁<78 M⁻¹ s⁻¹), r₂ remains constant (≈1). The constant magnitude of r₂ suggests that M₂* displays similar reactivity toward PS and any diluent. Meanwhile, since M₁* favors incorporating M₂ (r₁<1), gradient sequences result.

The copolymerization kinetics for PLA, PDMS, and PS collectively illustrate how different diluents can be used to control the graft polymer architecture. The magnitudes of r₁ and r₂ determine the backbone sequence, which can be alternating (r₁ r₂=0), blocky (r₁, r₂>>1), gradient (r₁>>r₂ or r₁<<r₂), or random (r₁=r₂=1).⁷⁶ The backbone sequence in turn directly determines the side chain distribution (FIG. 22A-22B). FIG. 32 illustrates the wide range of distributions obtained by copolymerizing PLA, PDMS, or PS with selected diluents. The relative reactivities of the macromonomers and diluents are interpreted in terms of the quotient r₁/r₂, which reflects the kinetic preference for the chain end (either M₁* or M₂*) to incorporate M₁ over M₂.

PLA/diluent copolymerizations obtain r₁/r₂ ranging from 0.20 (PLA+5a) to 5.8 (PLA+4a). Copolymerizing PDMS with 4a, one of the slowest-polymerizing diluents studied herein, produces a remarkably large difference between r₁ and r₂: r₁/r₂=19. This large disparity in reactivity results in a highly gradient—or blocky—distribution of side chains. Since r₁>>r₂, the graft polymers are densely grafted (i.e., rich in M₁) at early conversions and loosely grafted (i.e., rich in M₂) at later conversions. Copolymerizing PS with 5b, one of the fastest-polymerizing diluents introduced in this report, also affords a wide gap in reactivity: r₁/r₂=0.084. Compared to PDMS+4a, the inverse-tapered sequence is obtained. The ability to invert the gradient direction might not affect the properties of homopolymers, but it is valuable in the design of block polymers and other multicomponent materials. In the final section of this example, we demonstrate the physical consequences of varying the sequence distribution in the context of block polymer self-assembly.

Physical Consequences. Grafting density and graft distribution are important parameters that govern polymer architectures and physical properties. Grafting-through ring-opening metathesis copolymerization has recently been exploited to study how grafting density affects the scaling of the block polymer lamellar period.⁷⁸ In the final section of this example, we further demonstrate the utility of the ROMP method by describing the synthesis of AB diblock polymers with variable side chain distributions, then examine how differences in chain connectivity affect self-assembly.

Three different AB graft diblock polymers are synthesized by controlled ROMP. Simple substitutions of the discrete co-monomers ensure that the block polymers differ only in the distribution of the grafts for this series of experiments. All other aspects of the structure and chemistry are identical:

All block polymers of this particular series feature PDMS and PS side chains. The grafting-through approach guarantees that the side chain molecular weights are the same within each block (PDMS: 1280 g mol⁻¹, PS: 3990 g mol⁻¹).

The grafting density in each block is 50% for this particular series.

The backbone degree of polymerization in each block is the same. For the A block (PDMS+diluent), N_(bb,A)=150; for the B block (PS+diluent), N_(bb,B)=50.

The above constraints enforce equal block volume fractions for all three block polymers: f=0.50.

The side chain distributions can be varied while fixing all of the preceding parameters by switching the identity of the diluents in each block. FIG. 33A illustrates the resulting architectures with uniform (BP-1) or gradient (BP-2, BP-3) graft distributions. The backbones are drawn in the fully extended limit for ease of visualization, and the side chain conformations and cross-sectional radii are depicted as anticipated by existing theory.^(5,44-46)

BP-1 is synthesized by first copolymerizing PDMS and endo,exo-norbornenyl dimethylester (dx-DMeE, 1a) in a 1:1 feed ratio. Since r₁=1.1 and r₂=0.94, the first block has an ideal random backbone sequence and therefore uniform side chain distribution. After complete consumption of PDMS and dx-DMeE, the chain ends are still living, and the second block (B) is added via a 1:1 mixture of PS and endo,exo-norbornenyl di-n-butylester (dx-D^(n)BuE, 1d). Since r₁=0.80 and r₂=1.2, the side chain distribution in the second block is also effectively uniform. A graft polymer with a gradient side chain distribution (BP-2) is synthesized by keeping all conditions exactly the same but simply switching the diluents. The first block (A) is synthesized by copolymerizing PDMS with dx-D^(n)BuE instead of dx-DMeE; since r₁=1.1 and r₂=0.43, the block is rich in the macromonomer at early conversions and rich in the diluent at late conversions. Addition of PS+dx-DMeE as the second block (B; r₁=0.54, r₂=1.4) therefore produces a block polymer with low grafting density at the block-block junction and increasing grafting density moving toward the free chain ends. A third distinct graft block polymer (BP-3) is synthesized by keeping all conditions exactly the same as those for BP-2 but simply switching the order in which the blocks are added. By polymerizing block B (PS+dx-DMeE) first and block A (PDMS+dx-D^(n)BuE) second, the product features the inverse-tapered architecture compared to BP-2. FIG. 56 provides the chemical structures of BP-1, -2, and -3. Analysis by SEC (FIG. 57) and ¹H NMR (FIG. 58) confirms that their overall molecular weights and chemical compositions are identical.

These three graft block polymers are annealed for 24 hours at 140° C. under vacuum and modest applied pressure. The resulting microphase-separated structures are characterized by synchrotron-source small-angle X-ray scattering (SAXS). Comparison of the SAXS patterns (FIG. 33B) indicates that all three samples form long-range-ordered lamellar morphologies but also reveals two differences. First, the lamellar periods (d*=2n/q*) differ. Equal values of d* are perhaps expected since the chemical compositions and backbone and side chain lengths are all identical; on the contrary, BP-1 exhibits d*=51.0 nm (FIG. 33B.i), while BP-2 (FIG. 33B.ii) and BP-3 (FIG. 33B.iii) exhibit d*=49.5 and 46.5 nm, respectively. Second, the relative thicknesses of the A and B domains (d_(A) and d_(B)) also differ. Compared to BP-1, BP-2 forms more symmetric lamellae, as evidenced by the weak intensities of the even-order diffraction peaks (q₂, q₄, . . . ). The inverse-gradient BP-3 forms lamellae that are the most symmetric of all; in fact, the complete extinction of even-order peaks suggests that d_(A) and d_(B) are equal.

This symmetry is perhaps surprising: although the block volume fractions are equal (f=0.50), the backbone lengths are highly asymmetric: N_(bb,A)=3N_(bb,B). The graft polymer backbones are clearly not fully extended as illustrated in FIG. 33A. If the backbone is fully extended, d_(A)=3 d_(B) is contemplated for all samples (FIG. 34A). Every fourth diffraction peak (q₄, q₈, . . . ) would be weak, which is inconsistent with the SAXS data. Instead, the SAXS data indicates that the backbones are flexible and that changing the side chain distribution affects the backbone conformation. Gradient distributions in which the grafting density is either lowest (BP-2) or highest (BP-3) at the block-block junction enable more efficient packing than uniform distributions (BP-1). Closer packing balances the backbone asymmetry with the demands of equal block volumes, most likely via bending of the A (PDMS) block backbone (FIG. 34B).

For all samples, the backbones should be strongly stretched at the domain interface as a consequence of segregation. In the case of BP-2, the chains should have the highest local backbone stiffness but also the greatest free volume at the free chain ends. Compared to the uniformly grafted BP-1, this may better accommodate high grafting density in the center of the domains. In the case of BP-3, since the backbones are already strongly stretched at the domain interfaces, the high grafting density might not significantly stretch the backbones further, resulting in the smallest d* among all three graft polymers. Low grafting density at the free chain ends should result in comparatively low backbone stiffness and therefore better accommodate bending in the A block (FIG. 34C). Collectively, these results indicate that the side chain distribution affects chain stretching and packing. This result indicates that molecular “shape” is indeed an important design parameter, allowing materials to possess non-equilibrium density distributions.

Conclusion: Grafting-through methods of the present invention provide a versatile strategy for the design and synthesis of polymers with tailored side chain distributions. Controlled copolymerization of an &-norbornenyl macromonomer and a discrete norbornenyl diluent constructs graft architectures through the backbone; as a result, the backbone sequence directly dictates the side chain distribution. Since tuning the backbone sequence requires changing the relative reactivity of the co-monomers, we show steric and electronic effects on the homopolymerization kinetics of 23 diluents. Varying the stereochemistry, anchor groups, and substituents varies the homopolymerization rate constants over two orders of magnitude (0.36 M⁻¹ s⁻¹≤k_(homo)≤82 M⁻¹ s⁻¹), reflecting a wide scope of monomer reactivity. These small-molecule monomers can be readily prepared and diversified, providing a convenient library for future development. In order to provide further guidance, we identify rate trends and studied their origins through complementary mechanistic studies. Density functional theory (DFT) calculations suggest that formation of a Ru—O six-membered chelate (which sequesters the catalyst in an unproductive form) is significantly different for endo and exo isomers. Other factors that may affect the ROMP kinetics, including for example solvent quality and additives.

Building on these results, we studied the copolymerization kinetics of selected diluents and a poly(D,L-lactide) (PLA), polydimethylsiloxane (PDMS), or polystyrene (PS) macromonomer. The co-monomer concentrations are monitored by ¹H NMR, and the cross-propagation rate constants are calculated by non-linear least squares regression based on the Mayo-Lewis terminal model. Trends involving the measured self-propagation rate constants and the calculated reactivity ratios (r₁ and r₂) are identified. In general, for the 26 co-monomer pairs studied, the greater the difference between homopolymerization rates, the greater the gradient tendency (r₌₁/r₂>>1 or r₁/r₂<<1). The backbone sequence—and therefore the polymer architecture—can be tailored simply by choosing the appropriate diluent among the library introduced herein or by designing an appropriate monomer. We note that, at present, de novo prediction of the reactivity ratios from the macromonomer and diluent chemical structures is not possible. However, we anticipate that the versatility of this design strategy, coupled with the broad functional group tolerance of ROMP and its living character, should enable the design and synthesis of graft polymers with almost any desired graft chemistry and graft distribution.

We further demonstrate the ease and versatility of this approach by synthesizing three AB graft diblock polymers that differ in the distribution of side chains along the backbone. Analysis of the annealed, microphase-separated structures by small-angle X-ray scattering (SAXS) indicates that the graft block polymers all formed long-range-ordered lamellar structures. Differences in the lamellar periods and domain thicknesses reflect changes in the chain conformations. These results demonstrate the physical consequences of varying the side chain distribution. Ultimately, the design strategy outlined herein provides extensive customizability in terms of polymer structure and functionality, illuminating new opportunities for molecular and materials design.

REFERENCES CORRESPONDING TO EXAMPLE 2A

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Example 2B: Design, Synthesis, and Self-Assembly of Polymers with Tailored Graft Distributions

Materials and Methods:

General. Norbornene macromonomers PLA,¹ PDMS,² and PS³ were prepared according to reported procedures. Norbornene diluents were prepared according to reported procedures, summarized in Schemes 1-6. The second-generation ruthenium metathesis catalyst [(H₂IMes)(PCy₃)(Cl)₂Ru═CHPh] was generously provided by Materia, and G3 was prepared according to the reported procedure.⁴ CH₂Cl₂ was dried by passing through an activated alumina column. Deuterated solvents were purchased from Cambridge Isotopes Laboratories, Inc. and used as received.

NMR, SEC, and SAXS characterization. Ambient temperature NMR spectra were recorded on a Varian 400 MHz NMR spectrometer. Chemical shifts (6) were given in ppm and referenced against residual solvent signals (¹H, ¹³C). SEC data were collected using two Agilent PLgel MIXED-B 300×7.5 mm columns with 10 μm beads, connected to an Agilent 1260 Series pump, a Wyatt 18-angle DAWN HELEOS light scattering detector, and Optilab rEX differential refractive index detector. Online determination of dn/dc assumed 100% mass elution under the peak of interest. The mobile phase was THF. SAXS data were collected at beamline 12-ID at Argonne National Laboratory's Advanced Photon Source. The samples were probed using 12 keV (1.033 Å) X-rays, and the sample-to-detector distance was calibrated from a silver behenate standard. The beam was collimated using two sets of slits and a pinhole was used to remove parasitic scattering. The beam width was approximately 200-300 μm horizontally and 50 μm vertically.

Standard procedure for the determination of homopolymerization rate constants. A 4 mL vial was charged with a flea stir bar and the norbornene monomer (0.025 mmol) in CH₂Cl₂ at 298 K. While stirring vigorously, the polymerization was initiated by adding a CH₂Cl₂ solution of G3 (0.0125 M, 20 μL, 0.25 μmol) to achieve initial conditions of [norbornene]₀ (0.05 M) and [G3]₀ (0.5 mM). Over the course of the reaction, aliquots (˜20 μL) were extracted at different time points and immediately quenched in a separate vial containing a large excess of ethyl vinyl ether (˜0.2 mL) and silica-bound metal scavenger (SiliaMetS, dimercaptotriazine (DMT)) in THF. The quenched reaction mixtures were subsequentially subjected to SEC and ¹H NMR analysis, allowing the determination of [norbornene]_(t). For each homopolymerization experiment, the self-propagation rate constant k_(homo) was determined according to Eq. 1.

Standard procedure for the determination of copolymerization reactivity ratios. A 4 mL vial was charged with a flea stir bar and a CH₂Cl₂ solution of two norbornene monomers (M₁, M₂, each 0.025 mmol) at 298 K. While stirring vigorously, the copolymerization was initiated by adding a CH₂Cl₂ solution of G3 (0.0125 M, 20 μL, 0.25 μmol) to achieve initial conditions of [M₁]₀ (0.05 M), [M₂]₀ (0.05 M), and [G3]₀ (0.5 mM). Over the course of the reaction, aliquots (˜20 μL) were extracted at different time points and immediately quenched in a separate vial containing a large excess of ethyl vinyl ether (˜0.2 mL) and silica-bound metal scavenger (SiliaMetS, dimercaptotriazine (DMT)) in THF. The quenched reaction mixtures were subsequentially subjected to SEC and ¹H NMR analysis, allowing the determination of [M₁]_(t) and [M₂]_(t). Values of k₁₂ and k₂₁ were obtained by fitting the experimentally determined kinetic data with the best numerical solutions using MATLAB non-linear least-square solver (Isqcurvefit) in conjunction with non-stiff differential equation solver (ode45).²

Density functional theory. All calculations were carried out using version 4.0 of the ORCA package.⁵ For all complexes, the singlet potential energy surface was searched for minima in the gas phase using the BP86 exchange-correlation functional, along with the 6-31 G(d) basis set on all main group elements and the LANL2DZ basis set and associated effective core potential for Ru. For each structure, frequency calculations were carried out at the same level of theory to ensure true minima (no imaginary frequencies). To account for solvation effects, single point calculations were carried out on the optimized geometries using the SMD implicit solvation model (CH₂Cl₂) with the M06 functional in combination with the def2-TZVP basis set on Ru with the SDD pseudopotential, the 6-311+G(d,p) basis set on all heteroatoms and carbons in the primary coordination sphere of Ru, and the 6-31 G(d) basis set on all other C and H atoms. Free energies at 298.15 K were thus calculated as G=H^(BP86)−T×S^(BP86)+(E^(M06)−E^(BP86)), where H^(BP86), S^(BP86), E^(BP86) are the total enthalpy, entropy, and electronic energy calculated at the BP86 level, and E^(M06) is the electronic energy calculated at the M06 level. All calculations were carried out on a fine integration grid (ORCA Grid5, FinalGrid6).

Scheme 1 (illustrated above). Synthesis of 1a-1d. Cis-5-norbornene-endo,exo-2,3-dicarboxylic acid (5 g, 27.5 mmol) was added to 50 mL of the corresponding anhydrous alcohol. To this mixture was added ˜50 mg of conc. H₂SO₄. After stirring at 50° C. for 12 h, an excess of solid KHCO₃ was added to quench the reaction. The alcohol was removed under reduced pressure, and 30 mL CH₂Cl₂ was added. The organic solution was washed with brine (20 mL×3), dried with MgSO₄, and filtered to afford a colorless oil. The product was purified by either vacuum distillation or recrystallization from cold n-pentane.

Scheme 2 (illustrated above). Synthesis of 1e-1j. Cis-5-norbornene-endo,exo-2,3-diacyl chloride (3 mL, 18.5 mmol) was dissolved in CH₂Cl₂ (25 mL) and pyridine (4.91 mL, 61.0 mmol). A CH₂Cl₂ solution (5 mL) of the corresponding anhydrous alcohol (42.5 mmol) was slowly added at −78° C. The mixture was allowed to slowly warm to room temperature over 1 hour and was allowed to stir for 12 h. The pyridinium salt was removed by filtration. The organic solution was washed with brine (20 mL×3), dried with MgSO₄, and filtered to afford a colorless oil. The product was purified by either vacuum distillation or recrystallization from cold n-pentane.

Scheme 3 (illustrated above). Synthesis of 2a-2d. A suspension of cis-5-norbornene-endo,endo-2,3-dicarboxylic acid (2.0 g, 11 mmol), 4 drops of concentrated sulfuric acid, and 20 mL of the corresponding anhydrous alcohol was stirred under air at 75° C. After 36 hours, the solution was cooled to room temperature and was concentrated under reduced pressure. The resulting oil was redissolved in 50 mL CH₂Cl₂ and washed with saturated aqueous NaHCO₃ (2×30 mL) and brine (1×30 mL). The organic solution was dried over MgSO₄, filtered, and concentrated in vacuo to afford an oil. The oil was filtered through a plug of basic alumina, precipitated from cold (−78° C.) hexanes, and dried in vacuo to obtain the product as a white crystalline solid (2a), pink oil (2b-2c) or colorless oil (2d).

Scheme 4 (illustrated above). Synthesis of 3a-3d. A suspension of cis-5-norbornene-exo-2,3-dicarboxylic anhydride (2.00 g, 12.2 mmol), 4 drops of concentrated sulfuric acid, and 20 mL of the corresponding anhydrous alcohol was stirred under air at 75° C. After 20 hours, the colorless solution was cooled to room temperature and was concentrated under reduced pressure. The resulting pale yellow oil was redissolved in 50 mL CH₂Cl₂ and washed with saturated aqueous NaHCO₃ (2×30 mL) and brine (1×30 mL). The organic solution was dried over MgSO₄, filtered, and concentrated in vacuo to afford a colorless oil. Precipitation from cold (−78° C.) hexanes produced the product as a white crystalline solid (3a) or colorless oil (3b-3d) that was dried in vacuo.

Scheme 5 (illustrated above). Synthesis of 4a-4c. To a 10 mL MeCN solution of cis-5-norbornene-endo-2,3-diimide (1 g, 6.13 mmol) was added the corresponding alkyl halide (12.3 mmol) and K₂CO₃ (1.69 g, 12.3 mmol). The resulting mixture was allowed to stir at room temperature for 24 h (4a) or at 65° C. for 54 h (4b and 4c). The product was purified using column chromatography.

Scheme 6 (illustrated above). Synthesis of 5a-5c. To a 20 mL toluene solution of cis-5-norbornene-exo-2,3-dicarboxylic anhydride (1 g, 6.09 mmol) was added the corresponding alkyl amine (6.70 mmol) and Et₃N (0.85 mL, 0.609 mmol). The resulting mixture was allowed to stir at 110° C. for 15 h. The product was purified using column chromatography.

TABLE 4 Structures and homopolymerization rate constants (k_(homo)) for all monomers synthesized and studied in this report. Anchor Group ID R k_(homo) (M^(M−1) s⁻¹)

1a 1b 1c 1d 1e 1f 1g 1h 1i 1j Me Et nPr ^(n)Bu ^(i)Pr ^(i)Bu CH₂CF₃ Ph p-CF₃Ph p-MeOPh 18.7 14.6 10.4 6.90 6.14 5.32 10.5 8.36 5.14 7.76

2a 2b 2c 2d Me Et ^(n)Pr ^(n)Bu 2.24 0.934 0.518 0.362

3a 3b 3c 3d Me Et ^(n)Pr ^(n)Bu 30.8 16.4 11.2 10.4

4a 4b 4c Me ^(n)Bu ^(i)Bu 0.814 0.930 0.782

5a 5b 5c PDMS PLA PS Me ^(n)Bu Ph PDMS (1k) PLA (3k) PS (4k) 82.4 63.2 34.8 21.6 17.2 4.18

Derivation of Rate Expression (Eq. 2):

We derived a simplified rate expression corresponding to the proposed dissociative ROMP mechanism in which olefin coordination is the rate-limiting step:

The large value estimated for K_(eq,1)=k₁/k⁻¹ indicates that >99.8% of the precatalyst G3 exists as the monopyridine adduct in solution under the conditions employed in our homo- and copolymerization studies. The initial concentration of G3 equals the sum of the concentrations of the monopyridine adduct (“Ru-pyr”) and the 14-electron vacant species (“Ru”):

[G3]₀=[Ru−pyr]+[Ru]  (S1)

A steady-state approximation can be made for the 14-electron vacant species:

$\begin{matrix} {{- \frac{d\left\lbrack {Ru} \right\rbrack}{dt}} = {{{k_{2}\left\lbrack {{Ru} - {pyr}} \right\rbrack} - {{k_{- 2}\lbrack{Ru}\rbrack}\lbrack{pyr}\rbrack} - {{k_{3}\lbrack{Ru}\rbrack}\lbrack M\rbrack}} = 0}} & ({S2}) \end{matrix}$

Substituting S1 in S2 obtains the following:

$\begin{matrix} {{- \frac{d\left\lbrack {Ru} \right\rbrack}{dt}} = {{{k_{2}\left\lbrack {G3} \right\rbrack}_{0} - {k_{2}\left\lbrack {Ru} \right\rbrack} - {{k_{- 2}\lbrack{Ru}\rbrack}\lbrack{pyr}\rbrack} - {{k_{3}\lbrack{Ru}\rbrack}\lbrack M\rbrack}} = 0}} & ({S3}) \\ {\lbrack{Ru}\rbrack = \frac{{k_{2}\left\lbrack {G3} \right\rbrack}_{0}}{k_{2} + {k_{- 2}\left\lbrack {pyr} \right\rbrack} + {k_{3}\lbrack M\rbrack}}} & ({S4}) \\ {{\lbrack{Ru}\rbrack \times \frac{1/k_{- 2}}{1/k_{- 2}}} = {\frac{{K_{{eq}.\; 2}\left\lbrack {G3} \right\rbrack}_{0}}{K_{{eq}.\; 2} + \left\lbrack {pyr} \right\rbrack + {\frac{k_{3}}{k_{- 2}}\lbrack M\rbrack}} \approx \frac{{K_{{eq}.\; 2}\left\lbrack {G3} \right\rbrack}_{0}}{K_{{eq}.\; 2} + \left\lbrack {pyr} \right\rbrack}}} & ({S5}) \end{matrix}$

In Eq. S5, since k₃<<k⁻², the third term in the denominator is close to 0. The time-dependent consumption of the monomer (“M”) is provided by Eq. S6 (Eq. 2 in the main text):

$\begin{matrix} {{- \frac{d\lbrack M\rbrack}{dt}} = {{{k_{3}\lbrack{Ru}\rbrack}\lbrack M\rbrack} = {{\frac{K_{{eq}.\; 2}k_{3}}{K_{{eq}.\; 2} + \left\lbrack {pyr} \right\rbrack}\lbrack{G3}\rbrack}{0\;\lbrack M\rbrack}}}} & ({S6}) \end{matrix}$

TABLE 5 Compiled SEC data for PLA + diluent copolymerizations at full conversion. ID Diluent M_(n) (kDa)^(a) Ð 2d dd-D^(n)BuE 95.4 1.07 4c d-^(t)BuI 89.9 1.10 4a d-MeI 90.5 1.04 4b d-^(n)BuI 103 1.04 2a dd-DMeE 94.5 1.05 1d dx-D^(n)BuE 101 1.04 3d xx-D^(n)BuE —^(b) —^(b) 3c xx-D^(n)PrE 101 1.08 3b xx-DEtE 99.5 1.06 1a dx-DMeE 108 1.05 3a xx-DMeE 95.4 1.04 5b x-^(n)BuI 95.9 1.02 5a x-MeI 86.4 1.02

TABLE 6 Kinetic data for the copolymerization of PLA (M₁, M_(n) = 3230 g mol⁻¹) with selected diluents (M₂). The self-propagation rate constants k₂₂ and k₁₁ were determined from homopolymerization experiments, and the cross-propagation rate constants k₁₂ and k₂₁ were determined by fitting copolymerization data using non-linear least squares regression. The reactivity ratios r₁ = k₁₁/k₁₂ and r₂ = k₂₂/k₂₁ are also provided. k₂₂ k₁₁ k₁₂ k₂₁ ID Diluent (M⁻¹ s⁻¹) (M⁻¹ s⁻¹) (M⁻¹ s⁻¹) (M⁻¹ s⁻¹) r₁ r₂ r₁r₂ r₁/r₂ 2d dd-D^(n)BuE 0.362 17.2 8.03 0.860 2.14 0.421 0.902 5.09 4c d-^(t)BuI 0.782 17.2 11.0 1.72 1.56 0.455 0.708 3.43 4a d-MeI 0.814 17.2 4.55 1.24 3.78 0.656 2.48 5.76 4b d-^(n)BuI 0.930 17.2 8.14 1.08 2.11 0.861 1.82 2.45 2a dd-DMeE 2.24 17.2 8.05 2.71 2.14 0.827 1.77 2.58 1d dx-D^(n)BuE 6.90 17.2 16.4 7.35 1.05 0.939 0.983 1.12 3d xx-D^(n)BuE 10.4 17.2 46.0 8.94 0.374 1.17 0.436 0.320 3c xx-D^(n)PrE 11.2 17.2 47.2 9.38 0.364 1.20 0.436 0.304 3b xx-DEtE 16.4 17.2 48.6 10.1 0.354 1.63 0.577 0.217 1a dx-DMeE 18.7 17.2 18.0 15.7 0.953 1.19 1.13 0.801 3a xx-DMeE 30.8 17.2 49.2 18.3 0.350 1.68 0.588 0.208 5b x-^(n)BuI 63.2 17.2 27.2 21.4 0.633 2.95 1.87 0.214 5a x-MeI 82.4 17.2 28.4 27.1 0.606 3.05 1.85 0.199

TABLE 7 Kinetic data for the copolymerization of PDMS (M₁, M_(n) = 1280 mol⁻¹) with selected diluents (M₂). The self-propagation rate constants k₂₂ and k₁₁ were determined from homopolymerization experiments, and the cross-propagation rate constants k₁₂ and k₂₁ were determined by fitting copolymerization data using non-linear least squares regression. The reactivity ratios r₁ = k₁₁/k₁₂ and r₂ = k₂₂/k₂₁ are also provided. k₂₂ k₁₁ k₁₂ k₂₁ ID Diluent (M⁻¹ s⁻¹) (M⁻¹ s⁻¹) (M⁻¹ s⁻¹) (M⁻¹ s⁻¹) r₁ r₂ r₁r₂ r₁/r₂ 4a d-Mel 0.814 21.6 3.34 2.44 6.47 0.334 2.16 19.4 4b d-^(n)Bul 0.930 21.6 6.85 2.00 3.15 0.465 1.47 6.78 1d dx-D^(n)BuE 6.90 21.6 19.5 15.9 1.11 0.434 0.481 2.55 3d xx-D^(n)BuE 10.4 21.6 48.2 10.3 0.448 1.02 0.455 0.441 1a dx-DMeE 18.7 21.6 19.9 19.9 1.09 0.940 1.02 1.16 3a xx-DMeE 30.8 21.6 50.4 26.3 0.429 1.17 0.502 0.367

TABLE 8 Kinetic data for the copolymerization of PS (M₁, M_(n) = 3990 mol⁻¹) with selected diluents (M₂). The self-propagation rate constants k₂₂ and k₁₁ were determined from homopolymerization experiments, and the cross-propagation rate constants k₁₂ and k₂₁ were determined by fitting copolymerization data using non-linear least squares regression. The reactivity ratios r₁ = k₁₁/k₁₂ and r₂ = k₂₂/k₂₁ are also provided. k₂₂ k₁₁ k₁₂ k₂₁ ID Diluent (M⁻¹ s⁻¹) (M⁻¹ s⁻¹) (M⁻¹ s⁻¹) (M⁻¹ s⁻¹) r₁ r₂ r₁r₂ r₁/r₂ 1d dx-D^(n)BuE 6.90 4.18 5.23 5.66 0.799 1.22 0.974 0.656 3d xx-D^(n)BuE 10.4 4.18 29.9 7.58 0.140 1.38 0.193 0.102 1b dx-DEtE 14.6 4.18 7.77 8.75 0.538 1.67 0.897 0.322 1a dx-DMeE 18.7 4.18 7.74 13.2 0.540 1.42 0.765 0.381 3a xx-DMeE 30.8 4.18 30.8 23.3 0.136 1.32 0.180 0.103 5b x-^(n)Bul 63.2 4.18 30.8 38.9 0.136 1.63 0.221 0.0836 5a x-Mel 82.4 4.18 31.9 63.2 0.131 1.30 0.171 0.100

TABLE 9 Compiled SEC data for PDMS + diluent copolymerizations at full conversion. ID Diluent M_(n) (kDa)^(a) Ð 4a d-Mel 39.3 1.04 4b d-^(n)BuI 42.7 1.05 1d dx-D^(n)BuE 32.5 1.06 3d xx-D^(n)BuE 39.9 1.09 1a dx-DMeE 32.2 1.04 3a xx-DMeE 37.9 1.03 ^(a)The number-average molecular weight (M_(n)) is reported relative to polystyrene in THF (dn/dc = 0.185 mL g⁻¹).

TABLE 10 Compiled SEC data for PS + diluent copolymerizations at full conversion. ID Diluent M_(n) (kDa) Ð 1d dx-D^(n)BuE 362 1.09 3d xx-D^(n)BuE 379 1.09 1b dx-DEtE 398 1.10 1a dx-DMeE 375 1.04 3a xx-DMeE 376 1.05 5b x-^(n)BuI 386 1.04 5a x-MeI 364 1.06 ^(a)The number-average molecular weight (M_(n)) is reported relative to polystyrene in THF (dn/dc = 0.185 mL g⁻¹).

TABLE 11 xyz coordinates (in Angstroms) for structures in FIG. 53: endo isomer (2a). olefin endo (2a) C 1.37924E+00  3.92831E−01 −3.22856E−01  C 1.16270E+00 −9.39169E−01 −2.65412E−01  O −9.72876E−02   2.15024E+00 −2.19202E+00  O −2.27946E+00   1.48833E+00 −2.26447E+00  O −2.43997E+00  −2.31171E+00 −1.62638E+00  O −7.30496E−01  −1.10449E+00 −2.52547E+00  C 2.79507E−01  1.06702E+00 4.86745E−01 C −8.10609E−02  −1.16530E+00 5.81677E−01 C −1.34579E+00  −6.49205E−01 −2.42913E−01  C −1.06624E+00   9.05880E−01 −3.14351E−01  H −1.88335E+00   1.40366E+00 2.40453E−01 H −2.24511E+00  −8.32600E−01 3.65716E−01 C 5.39175E−02  3.47364E−03 1.59193E+00 H −8.54421E−01   1.72316E−01 2.19954E+00 H 9.29488E−01 −1.12527E−01 2.25139E+00 H −2.30996E−01  −2.17697E+00 9.87862E−01 H 1.69050E+00 −1.71993E+00 −8.18140E−01  H 2.11273E+00  9.23746E−01 −9.31238E−01  H 4.70643E−01  2.10252E+00 8.04631E−01 C −1.04361E+00   1.56452E+00 −1.68620E+00  C −1.59258E+00  −1.43417E+00 −1.52086E+00  C −2.37037E+00   2.10899E+00 −3.56562E+00  H −3.40808E+00   1.95389E+00 −3.89040E+00  H −1.66592E+00   1.63678E+00 −4.26851E+00  H −2.13915E+00   3.18414E+00 −3.49946E+00  C −9.05792E−01  −1.87012E+00 −3.73855E+00  H −1.53347E−01  −1.48092E+00 −4.43738E+00  H −1.92285E+00  −1.73248E+00 −4.13837E+00  H −7.43190E−01  −2.94249E+00 −3.54617E+00  chelate endo (FIG. 52A) Ru 2.51298E+00 −2.83991E+00 1.99790E+00 C 1.82535E+00 −1.48956E+00 9.77774E−01 C 4.28400E+00 −3.09559E+00 1.11161E+00 N 5.17130E+00 −4.03946E+00 1.57214E+00 N 4.89236E+00 −2.45658E+00 6.42919E−02 O 6.65926E−01 −2.84820E+00 3.19021E+00 O −1.22902E+00  −1.98641E+00 4.03640E+00 O −3.33328E+00  −9.09042E−01 1.02780E+00 O −1.34432E+00  −2.01365E+00 8.26982E−01 Cl 3.35846E+00 −1.34486E+00 3.70978E+00 Cl 1.46186E+00 −4.58682E+00 6.51703E−01 C −8.27318E−01   1.20405E+00 1.15747E+00 C 1.10551E+00 −2.91703E−01 1.54542E+00 C −1.33078E+00   2.74034E−02 2.06495E+00 C 4.88660E−03 −5.18496E−01 2.65677E+00 C 6.49035E+00 −3.97113E+00 9.08613E−01 C 6.21706E+00 −3.02710E+00 −2.74732E−01  H 6.16629E+00 −3.56374E+00 −1.24047E+00  C 4.36805E+00 −1.40755E+00 −7.63900E−01  C 4.06401E−01  5.80081E−01 4.62618E−01 C 4.98068E+00 −4.91335E+00 2.70433E+00 H 7.24820E+00 −3.56608E+00 1.60497E+00 C −1.84115E+00   1.80210E+00 2.20939E−01 C −2.16952E+00   3.10431E+00 1.92397E−01 H 1.08210E+00  1.34434E+00 4.65121E−02 H 7.63865E−02 −5.74638E−02 −3.78048E−01  C −2.13755E+00  −9.97183E−01 1.26637E+00 H −4.79652E−01   1.99676E+00 1.84913E+00 H 1.91235E+00  2.89956E−01 2.03916E+00 H −1.72188E+00   3.82750E+00 8.85133E−01 H −2.31842E+00   1.11183E+00 −4.87369E−01  C 3.68129E+00 −1.73937E+00 −1.95803E+00  C 3.23637E+00 −6.86731E−01 −2.77795E+00  C 3.46294E+00  6.63162E−01 −2.45071E+00  C 4.15083E+00  9.51903E−01 −1.25857E+00  C 4.48041E+00 −6.22311E+00 2.47903E+00 C 4.31315E+00 −7.06877E+00 3.58927E+00 C 4.65216E+00 −6.66730E+00 4.89346E+00 C 5.22464E+00 −5.39627E+00 5.06633E+00 C 5.42086E+00 −4.50989E+00 3.99150E+00 C 4.17339E+00 −6.72798E+00 1.08927E+00 C 6.16339E+00 −3.21319E+00 4.22168E+00 C 4.41365E+00 −7.58229E+00 6.07529E+00 C 3.38799E+00 −3.17708E+00 −2.32345E+00  C 3.00658E+00  1.77196E+00 −3.37533E+00  H 3.94729E+00 −7.80665E+00 1.11444E+00 H 5.02776E+00 −6.57808E+00 4.04097E−01 H 7.24393E+00 −3.34406E+00 4.01488E+00 H 5.77851E+00 −2.39554E+00 3.59550E+00 H 5.12597E+00 −7.38190E+00 6.89345E+00 H 4.50600E+00 −8.64426E+00 5.79043E+00 H 2.81445E+00 −3.22809E+00 −3.26333E+00  H 4.31332E+00 −3.76410E+00 −2.46948E+00  C 4.61915E+00 −6.23716E−02 −4.02344E−01  C 5.35853E+00  2.81360E−01 8.70892E−01 H 5.48020E+00  1.37280E+00 9.66800E−01 H 4.82436E+00 −9.09074E−02 1.76445E+00 H 2.06051E+00  1.51394E+00 −3.88083E+00  H 2.85646E+00  2.71858E+00 −2.82975E+00  H 6.96712E+00 −2.22401E+00 −3.68618E−01  H 6.81553E+00 −4.97614E+00 5.91689E−01 H 6.06886E+00 −2.89276E+00 5.27154E+00 H 3.30519E+00 −6.19909E+00 6.58265E−01 H 3.39607E+00 −7.44241E+00 6.48566E+00 H 2.80459E+00 −3.68471E+00 −1.53222E+00  H 3.75553E+00  1.96491E+00 −4.16631E+00  H 6.36774E+00 −1.69857E−01 8.90609E−01 H 5.54415E+00 −5.08207E+00 6.06744E+00 H 3.91613E+00 −8.07764E+00 3.42344E+00 H 4.33820E+00  1.99804E+00 −9.86679E−01  H 2.69471E+00 −9.31865E−01 −3.69981E+00  H 1.88651E+00 −1.51676E+00 −1.26084E−01  C −1.21050E−01  −1.89760E+00 3.27451E+00 C −1.99960E+00  −3.05629E+00 6.19953E−02 H −2.34427E+00  −2.65356E+00 −9.03869E−01  H −1.22663E+00  −3.82375E+00 −7.39152E−02  H −2.86600E+00  −3.44543E+00 6.18671E−01 C −1.42371E+00  −3.25544E+00 4.71500E+00 H −5.99728E−01  −3.43623E+00 5.42191E+00 H −1.46447E+00  −4.07564E+00 3.98287E+00 H −2.37950E+00  −3.14886E+00 5.24370E+00 H −2.90057E+00   3.49776E+00 −5.21047E−01  H −2.00732E+00   4.03936E−01 2.84711E+00 H 2.57913E−01  1.35145E−01 3.51335E+00 vacant endo (FIG. 52B) Ru 2.95468E+00 −2.53803E+00 2.28144E+00 C 1.60566E+00 −1.74763E+00 1.33824E+00 C 4.25479E+00 −3.10926E+00 9.54312E−01 O −1.47766E+00  −3.12470E+00 −1.78657E−02  O −1.38177E+00  −8.53069E−01 −1.60651E−01  O −3.80276E+00  −1.29270E+00 1.44332E+00 O −4.00359E+00  −5.02317E−01 3.57129E+00 N 4.41627E+00 −2.73169E+00 −3.55362E−01  N 5.31358E+00 −3.92952E+00 1.27572E+00 Cl 4.17252E+00 −6.35523E−01 2.99402E+00 Cl 1.88733E+00 −4.56009E+00 2.85127E+00 C −1.15394E+00   5.61245E−01 2.71186E+00 C 5.02974E−01 −1.21251E+00 2.20505E+00 C −1.80078E+00  −8.91894E−01 2.81262E+00 C −9.11992E−01  −1.85880E+00 1.98350E+00 C 6.32000E+00 −4.00325E+00 1.96801E−01 C 5.56275E+00 −3.41225E+00 −1.00153E+00  H 5.19893E+00 −4.18985E+00 −1.70002E+00  C 3.53251E+00 −1.97819E+00 −1.20169E+00  C 2.50457E−01  3.14172E−01 2.07030E+00 C 5.55112E+00 −4.61622E+00 2.52205E+00 H 7.21204E+00 −3.40662E+00 4.65074E−01 C −1.96203E+00   1.57297E+00 1.93985E+00 C −2.40276E+00   2.73731E+00 2.44461E+00 H 1.04373E+00  8.99830E−01 2.56055E+00 H 2.31510E−01  5.89616E−01 1.00329E+00 C −3.28843E+00  −9.36306E−01 2.49572E+00 H −1.02968E+00   9.37301E−01 3.74209E+00 H 7.50605E−01 −1.41727E+00 3.27034E+00 H −2.20977E+00   3.02414E+00 3.48549E+00 H −2.16978E+00   1.31323E+00 8.94143E−01 C 2.48456E+00 −2.64422E+00 −1.88085E+00  C 1.72157E+00 −1.90381E+00 −2.80386E+00  C 1.96993E+00 −5.43129E−01 −3.05726E+00  C 3.01363E+00  8.53800E−02 −2.35303E+00  C 5.06969E+00 −5.94251E+00 2.65841E+00 C 5.32820E+00 −6.62153E+00 3.86077E+00 C 6.05872E+00 −6.03408E+00 4.90796E+00 C 6.58109E+00 −4.74460E+00 4.70815E+00 C 6.36246E+00 −4.02146E+00 3.52167E+00 C 4.32435E+00 −6.63275E+00 1.53902E+00 C 7.04596E+00 −2.68784E+00 3.31908E+00 C 6.28216E+00 −6.76818E+00 6.21230E+00 C 2.16693E+00 −4.09847E+00 −1.61050E+00  C 1.13445E+00  2.32851E−01 −4.05336E+00  H 4.09469E+00 −7.67461E+00 1.81498E+00 H 4.91727E+00 −6.65664E+00 6.05811E−01 H 7.91535E+00 −2.78875E+00 2.64073E+00 H 6.36840E+00 −1.92866E+00 2.89799E+00 H 5.61421E+00 −6.38045E+00 7.00355E+00 H 7.31792E+00 −6.64661E+00 6.57454E+00 H 1.29919E+00 −4.42430E+00 −2.20529E+00  H 3.01431E+00 −4.76256E+00 −1.86081E+00  C 3.81193E+00 −6.08298E−01 −1.42719E+00  C 4.93276E+00  9.29668E−02 −6.94324E−01  H 4.79705E+00  3.10315E−02 4.00004E−01 H 5.91708E+00 −3.56224E−01 −9.22937E−01  H 4.49712E−01  9.34478E−01 −3.54223E+00  H 1.76791E+00  8.36326E−01 −4.72674E+00  H 6.16135E+00 −2.68648E+00 −1.57567E+00  H 6.63664E+00 −5.04683E+00 3.67537E−02 H 7.42750E+00 −2.30093E+00 4.27787E+00 H 3.37207E+00 −6.12160E+00 1.32306E+00 H 6.07913E+00 −7.84699E+00 6.10889E+00 H 1.92755E+00 −4.26532E+00 −5.45493E−01  H 5.20093E−01 −4.38764E−01 −4.67540E+00  H 4.97806E+00  1.15622E+00 −9.80752E−01  H 7.19303E+00 −4.28486E+00 5.49388E+00 H 4.94472E+00 −7.64174E+00 3.98046E+00 H 3.22223E+00  1.14671E+00 −2.53519E+00  H 9.16749E−01 −2.41390E+00 −3.34692E+00  H 1.51773E+00 −1.64027E+00 2.44568E−01 C −1.30062E+00  −2.04026E+00 5.14509E−01 C −5.43205E+00  −4.37513E−01 3.35661E+00 H −5.66679E+00   2.72112E−01 2.54765E+00 H −5.82817E+00  −1.43007E+00 3.09048E+00 H −5.85265E+00  −9.20309E−02 4.31036E+00 C −1.88096E+00  −9.79092E−01 −1.51052E+00  H −2.89432E+00  −1.40903E+00 −1.49279E+00  H −1.21812E+00  −1.62188E+00 −2.10945E+00  H −1.89848E+00   4.37867E−02 −1.91075E+00  H −2.96947E+00   3.45072E+00 1.83703E+00 H −1.70276E+00  −1.19840E+00 3.86845E+00 H −9.28168E−01  −2.87539E+00 2.40434E+00 olefin adduct endo (FIG. 52C) Ru 2.78629E+00 −2.64299E+00 2.55817E+00 C 1.40559E+00 −1.91739E+00 1.58761E+00 C 4.19891E+00 −3.06497E+00 1.05222E+00 C 2.07251E+00 −1.85353E+00 4.62129E+00 C 1.34854E+00 −3.02166E+00 4.35842E+00 N 5.35550E+00 −3.73648E+00 1.33089E+00 N 4.19961E+00 −2.78281E+00 −2.78811E−01  O −3.11283E+00   2.08198E+00 2.74260E+00 O −3.58219E+00  −1.02816E−01 2.29459E+00 O −1.85751E+00  −2.78398E+00 2.90201E+00 O −1.78179E+00  −1.94838E+00 7.88705E−01 O −7.46843E−01  −2.21975E+00 6.62167E+00 O −8.90751E−01  −4.49262E+00 6.59710E+00 O 1.46586E+00  1.12303E−02 6.90170E+00 O 9.81721E−01 −1.22240E+00 8.76094E+00 Cl 3.97967E+00 −4.87109E−01 2.80845E+00 Cl 1.86702E+00 −4.88353E+00 2.05216E+00 C −7.63334E−01   1.14821E+00 7.97353E−01 C 7.36835E−01 −5.85949E−01 1.78544E+00 C −1.26244E+00   6.99678E−01 2.23644E+00 C −6.54225E−01  −6.99878E−01 2.52766E+00 C 6.25818E+00 −3.84925E+00 1.58549E−01 C 5.36745E+00 −3.36541E+00 −9.92028E−01  H 5.02861E+00 −4.18808E+00 −1.64747E+00  C 3.24746E+00 −2.06619E+00 −1.08981E+00  C 3.90226E−01  1.48053E−01 4.64568E−01 C 5.81371E+00 −4.27055E+00 2.59319E+00 H 7.14739E+00 −3.21049E+00 3.08187E−01 C −1.82454E+00   1.15814E+00 −2.74283E−01  C −2.15163E+00   2.23372E+00 −1.01164E+00  H 1.27109E+00  6.59852E−01 4.93272E−02 H 4.90200E−02 −5.81194E−01 −2.88432E−01  C −2.76816E+00   8.03028E−01 2.42439E+00 H −3.61279E−01   2.17187E+00 8.90788E−01 H 1.37384E+00  6.35766E−02 2.40940E+00 H −1.66527E+00   3.20525E+00 −8.60680E−01  H −2.33176E+00   2.00303E−01 −4.45755E−01  C 2.21194E+00 −2.77794E+00 −1.74424E+00  C 1.38549E+00 −2.06842E+00 −2.63627E+00  C 1.57934E+00 −7.04538E−01 −2.91522E+00  C 2.65009E+00 −4.59131E−02 −2.28439E+00  C 5.58442E+00 −5.64439E+00 2.87541E+00 C 6.07086E+00 −6.16071E+00 4.08890E+00 C 6.80886E+00 −5.37764E+00 4.99455E+00 C 7.08935E+00 −4.04786E+00 4.64077E+00 C 6.63050E+00 −3.47544E+00 3.43876E+00 C 4.88643E+00 −6.55632E+00 1.89459E+00 C 7.06311E+00 −2.07744E+00 3.06386E+00 C 7.33719E+00 −5.97276E+00 6.28263E+00 C 2.00389E+00 −4.25926E+00 −1.52944E+00  C 6.48412E−01  4.42692E−02 −3.84378E+00  H 4.79510E+00 −7.57197E+00 2.31265E+00 H 5.45478E+00 −6.63947E+00 9.48736E−01 H 7.72907E+00 −2.09126E+00 2.18014E+00 H 6.20436E+00 −1.42568E+00 2.82960E+00 H 7.62389E+00 −5.18851E+00 7.00260E+00 H 8.23291E+00 −6.59466E+00 6.09726E+00 H 1.10660E+00 −4.60483E+00 −2.06839E+00  H 2.86014E+00 −4.84751E+00 −1.91041E+00  C 3.49755E+00 −6.99148E−01 −1.37227E+00  C 4.64514E+00  4.41322E−02 −7.28988E−01  H 4.57008E+00  1.84599E−02 3.73206E−01 H 5.62380E+00 −3.95567E−01 −9.99253E−01  H −1.36006E−01   5.71389E−01 −3.26842E+00  H 1.18891E+00  8.06109E−01 −4.43136E+00  H 5.84813E+00 −2.59896E+00 −1.62082E+00  H 6.59668E+00 −4.89081E+00 3.71591E−02 H 7.62871E+00 −1.61644E+00 3.88988E+00 H 3.87557E+00 −6.18705E+00 1.65166E+00 H 6.58730E+00 −6.62357E+00 6.76441E+00 H 1.89100E+00 −4.51489E+00 −4.60103E−01  H 1.42005E−01 −6.37672E−01 −4.54735E+00  H 4.65590E+00  1.09648E+00 −1.05666E+00  H 7.70244E+00 −3.43214E+00 5.30988E+00 H 5.87795E+00 −7.21492E+00 4.32200E+00 H 2.83528E+00  1.01228E+00 −2.50625E+00  H 5.74435E−01 −2.60868E+00 −3.13957E+00  H 8.98947E−01 −2.57615E+00 8.53466E−01 C −1.50687E+00  −1.90663E+00 2.12306E+00 C −4.53536E+00   2.30573E+00 2.87305E+00 H −5.04697E+00   2.09101E+00 1.92155E+00 H −4.95651E+00   1.66170E+00 3.66096E+00 H −4.63830E+00   3.36611E+00 3.13943E+00 C −2.62098E+00  −3.05949E+00 3.92081E−01 H −3.59913E+00  −2.98325E+00 8.91269E−01 H −2.14436E+00  −4.01510E+00 6.58485E−01 H −2.72987E+00  −2.96480E+00 −6.96700E−01  H −2.91983E+00   2.18609E+00 −1.79081E+00  H −8.04128E−01   1.39782E+00 2.95718E+00 H −5.02469E−01  −8.27154E−01 3.61031E+00 C 3.04840E+00 −2.18330E+00 5.74754E+00 C 1.84765E+00 −4.07133E+00 5.34263E+00 C 1.28835E+00 −3.58683E+00 6.75395E+00 C 2.19235E+00 −2.32987E+00 7.05505E+00 H 2.86947E+00 −2.60819E+00 7.88386E+00 H 1.45811E+00 −4.38611E+00 7.49508E+00 C 3.33446E+00 −3.68003E+00 5.47683E+00 H 3.85627E+00 −4.18635E+00 6.30725E+00 H 3.90853E+00 −3.86685E+00 4.54876E+00 H 1.60501E+00 −5.11423E+00 5.10228E+00 H 3.45960E−01 −3.07675E+00 3.92794E+00 H 1.74552E+00 −8.30441E−01 4.44418E+00 H 3.90692E+00 −1.50520E+00 5.84463E+00 C 1.49289E+00 −1.05165E+00 7.50529E+00 C −2.07807E−01  −3.31873E+00 6.67485E+00 C 2.33090E−01 −9.06581E−02 9.25278E+00 H −8.32188E−02  −3.68259E−01 1.02678E+01 H −6.41548E−01   8.91697E−02 8.60790E+00 H 8.60721E−01  8.14495E−01 9.27324E+00 C −2.30831E+00  −4.34057E+00 6.32983E+00 H −2.70080E+00  −5.36493E+00 6.27772E+00 H −2.45521E+00  −3.81210E+00 5.37522E+00 H −2.79452E+00  −3.77682E+00 7.14170E+00 metallacyclobutane endo (FIG. 52D) Ru 2.48432E+00 −2.45240E+00 2.26077E+00 C 5.04808E−01 −1.94731E+00 2.29378E+00 C 4.08056E+00 −2.81180E+00 1.03692E+00 C 2.27404E+00 −2.66601E+00 4.22552E+00 C 8.41763E−01 −2.00079E+00 3.82367E+00 N 5.18936E+00 −3.44965E+00 1.49947E+00 N 4.25495E+00 −2.52706E+00 −2.79432E−01  O −3.43500E+00   2.57195E+00 8.30333E−01 O −4.23411E+00   4.92799E−01 1.31388E+00 O −2.98984E+00  −2.03839E+00 3.06256E+00 O −2.60902E+00  −1.94667E+00 8.22609E−01 O 9.64500E−01 −4.28823E−01 6.51783E+00 O −1.20064E+00  −9.14663E−01 7.03891E+00 O 3.67828E+00 −2.50757E+00 7.00893E+00 O 1.96990E+00 −2.38579E+00 8.51498E+00 Cl 3.18321E+00 −1.55039E−01 2.69746E+00 Cl 1.74965E+00 −4.65973E+00 1.43527E+00 C −1.04194E+00   7.09439E−01 −5.49562E−02  C −2.40763E−02  −6.19749E−01 1.78173E+00 C −1.81627E+00   9.20249E−01 1.32258E+00 C −1.50472E+00  −3.07422E−01 2.21411E+00 C 6.25751E+00 −3.53213E+00 4.73361E−01 C 5.52558E+00 −3.09303E+00 −8.04775E−01  H 5.30438E+00 −3.93884E+00 −1.47999E+00  C 3.40892E+00 −1.78757E+00 −1.18678E+00  C −4.96489E−02  −4.59556E−01 2.44997E−01 C 5.45708E+00 −3.89372E+00 2.84900E+00 H 7.09131E+00 −2.85800E+00 7.42305E−01 C −1.93924E+00   4.40666E−01 −1.23693E+00  C −2.12963E+00   1.29309E+00 −2.25975E+00  H 9.56394E−01 −2.53374E−01 −1.52722E−01  H −4.09857E−01  −1.38946E+00 −2.25452E−01  C −3.28989E+00   1.25903E+00 1.16944E+00 H −4.82666E−01   1.63899E+00 −2.57848E−01  H 5.97251E−01  1.87812E−01 2.20782E+00 H −1.62792E+00   2.26779E+00 −2.29788E+00  H −2.46975E+00  −5.19504E−01 −1.22011E+00  C 2.51612E+00 −2.48319E+00 −2.04105E+00  C 1.79007E+00 −1.73457E+00 −2.98465E+00  C 1.94783E+00 −3.44815E−01 −3.12470E+00  C 2.88098E+00  3.00733E−01 −2.29517E+00  C 5.27303E+00 −5.26178E+00 3.16869E+00 C 5.56333E+00 −5.67523E+00 4.48268E+00 C 6.04784E+00 −4.78610E+00 5.45637E+00 C 6.29287E+00 −3.45555E+00 5.07598E+00 C 6.02452E+00 −2.98555E+00 3.78009E+00 C 4.80771E+00 −6.26923E+00 2.14341E+00 C 6.35728E+00 −1.55770E+00 3.41489E+00 C 6.29943E+00 −5.23408E+00 6.87895E+00 C 2.36665E+00 −3.98589E+00 −1.99751E+00  C 1.13354E+00  4.29095E−01 −4.13711E+00  H 4.70478E+00 −7.26578E+00 2.60325E+00 H 5.52878E+00 −6.36619E+00 1.30958E+00 H 6.99858E+00 −1.50061E+00 2.51619E+00 H 5.44825E+00 −9.64590E−01 3.20867E+00 H 5.58862E+00 −4.73923E+00 7.56489E+00 H 7.31617E+00 −4.96397E+00 7.21586E+00 H 1.51920E+00 −4.30619E+00 −2.62545E+00  H 3.27006E+00 −4.49107E+00 −2.39013E+00  C 3.63278E+00 −3.94452E−01 −1.33013E+00  C 4.66476E+00  3.36499E−01 −5.03722E−01  H 4.38736E+00  3.42137E−01 5.65553E−01 H 5.66259E+00 −1.33399E−01 −5.81377E−01  H 1.31114E−01  6.62407E−01 −3.73108E+00  H 1.61802E+00  1.38395E+00 −4.40195E+00  H 6.07087E+00 −2.32451E+00 −1.37585E+00  H 6.64784E+00 −4.56074E+00 4.15842E−01 H 6.90037E+00 −1.07066E+00 4.24087E+00 H 3.83396E+00 −5.98096E+00 1.71146E+00 H 6.18153E+00 −6.32483E+00 6.98972E+00 H 2.19795E+00 −4.35346E+00 −9.70925E−01  H 9.84965E−01 −1.50609E−01 −5.06448E+00  H 4.76074E+00  1.38042E+00 −8.44105E−01  H 6.69864E+00 −2.75298E+00 5.81238E+00 H 5.40965E+00 −6.72905E+00 4.74557E+00 H 3.04668E+00  1.37871E+00 −2.41054E+00  H 1.09101E+00 −2.26393E+00 −3.64341E+00  H −8.72236E−02  −2.81318E+00 1.95135E+00 C −2.46196E+00  −1.49481E+00 2.09950E+00 C −4.79937E+00   2.97952E+00 5.81839E−01 H −5.22145E+00   2.41128E+00 −2.61978E−01  H −5.42268E+00   2.81254E+00 1.47448E+00 H −4.74307E+00   4.04938E+00 3.40043E−01 C −3.54164E+00  −3.04393E+00 6.81876E−01 H −4.54880E+00  −2.71742E+00 9.83468E−01 H −3.23113E+00  −3.89786E+00 1.30304E+00 H −3.51873E+00  −3.30831E+00 −3.83770E−01  H −2.80054E+00   1.05386E+00 −3.09193E+00  H −1.34375E+00   1.79252E+00 1.80666E+00 H −1.54495E+00  −3.00760E−02 3.27976E+00 C 1.90753E+00 −3.91633E+00 5.03193E+00 C −1.10395E−01  −2.93941E+00 4.63922E+00 C 1.00901E−01 −2.69830E+00 6.18324E+00 C 1.47141E+00 −3.43883E+00 6.45741E+00 H 1.22574E+00 −4.34393E+00 7.04542E+00 H −7.21075E−01  −3.21592E+00 6.70250E+00 C 5.27060E−01 −4.33453E+00 4.48227E+00 H 2.61521E−02 −5.09491E+00 5.10859E+00 H 5.65576E−01 −4.68628E+00 3.44304E+00 H −1.16362E+00  −2.82792E+00 4.34178E+00 H 8.95414E−01 −9.59943E−01 4.17690E+00 H 2.92543E+00 −1.95106E+00 4.74672E+00 H 2.70157E+00 −4.67707E+00 5.05316E+00 C 2.50763E+00 −2.70850E+00 7.30055E+00 C 4.69337E−02 −1.23876E+00 6.59711E+00 C 2.85856E+00 −1.65135E+00 9.38578E+00 H 2.29281E+00 −1.49582E+00 1.03145E+01 H 3.12675E+00 −6.87427E−01 8.92581E+00 H 3.77693E+00 −2.22745E+00 9.58079E+00 C −1.37000E+00   4.74700E−01 7.40082E+00 H −2.41999E+00   5.67678E−01 7.70822E+00 H −1.15484E+00   1.12916E+00 6.54151E+00 H −6.94240E−01   7.41666E−01 8.22879E+00 pyridine adduct endo(FIG. 52E) Ru 3.05288E+00 −2.28463E+00 2.52684E+00 C 1.67715E+00 −1.41400E+00 1.67128E+00 C 4.09879E+00 −3.07536E+00 9.87837E−01 N 5.05130E+00 −4.02595E+00 1.28793E+00 N 4.24184E+00 −2.78066E+00 −3.38327E−01  N 2.53498E+00 −1.59335E+00 4.60362E+00 O −4.43645E+00  −1.81721E+00 2.35141E+00 O −3.67745E+00  −7.65497E−01 4.78694E−01 O −8.48756E−01   6.27190E−02 −1.42354E−01  O −1.21369E+00  −2.00026E+00 −1.03967E+00  Cl 4.56546E+00 −3.60281E−01 2.39956E+00 Cl 1.70118E+00 −4.29090E+00 2.90579E+00 C −1.66970E+00  −2.46136E−02 2.98809E+00 C 2.90238E−01 −1.34350E+00 2.25314E+00 C −2.10985E+00  −1.37379E+00 2.26731E+00 C −9.12386E−01  −1.81754E+00 1.36481E+00 C 5.99433E+00 −4.26048E+00 1.73780E−01 C 5.22789E+00 −3.66666E+00 −1.01000E+00  H 4.69321E+00 −4.43638E+00 −1.59898E+00  C 3.41417E+00 −1.99595E+00 −1.21599E+00  C −1.32736E−01   7.79299E−02 2.71811E+00 C 5.29872E+00 −4.64233E+00 2.56878E+00 H 6.94856E+00 −3.73322E+00 3.64511E−01 C −2.40708E+00   1.21760E+00 2.55806E+00 C −3.10065E+00   2.01093E+00 3.39179E+00 H 4.12862E−01  3.90367E−01 3.62200E+00 H 6.82121E−02  8.15827E−01 1.92544E+00 C −3.45784E+00  −1.27659E+00 1.57010E+00 H −1.84434E+00  −1.65896E−01 4.06935E+00 H 2.61035E−01 −2.01104E+00 3.13142E+00 H −3.19119E+00   1.78468E+00 4.46150E+00 H −2.33714E+00   1.46911E+00 1.49314E+00 C 2.20334E+00 −2.53885E+00 −1.70688E+00  C 1.53129E+00 −1.83820E+00 −2.72807E+00  C 2.03501E+00 −6.43801E−01 −3.27006E+00  C 3.22761E+00 −1.20825E−01 −2.73643E+00  C 4.74257E+00 −5.92819E+00 2.80876E+00 C 5.00007E+00 −6.54473E+00 4.04211E+00 C 5.80324E+00 −5.93902E+00 5.02726E+00 C 6.39648E+00 −4.70366E+00 4.72750E+00 C 6.18825E+00 −4.04592E+00 3.49761E+00 C 3.91833E+00 −6.63802E+00 1.76018E+00 C 6.98336E+00 −2.79958E+00 3.17833E+00 C 6.04189E+00 −6.62294E+00 6.35669E+00 C 1.64797E+00 −3.85003E+00 −1.19368E+00  C 1.33497E+00  5.29615E−02 −4.41914E+00  H 3.64498E+00 −7.64883E+00 2.10430E+00 H 4.47094E+00 −6.74493E+00 8.08683E−01 H 7.84115E+00 −3.04632E+00 2.52286E+00 H 6.38367E+00 −2.02233E+00 2.67814E+00 H 6.71950E+00 −6.03473E+00 6.99723E+00 H 6.48918E+00 −7.62432E+00 6.22064E+00 H 5.85002E−01 −3.94340E+00 −1.46469E+00  H 2.18673E+00 −4.71356E+00 −1.62977E+00  C 3.93930E+00 −7.77578E−01 −1.71901E+00  C 5.23592E+00 −2.01323E−01 −1.19808E+00  H 5.22122E+00 −1.19252E−01 −9.72136E−02  H 6.10521E+00 −8.31437E−01 −1.46670E+00  H 1.21447E+00  1.13436E+00 −4.22887E+00  H 1.91595E+00 −4.39110E−02 −5.35518E+00  H 5.86432E+00 −3.08480E+00 −1.69483E+00  H 6.20511E+00 −5.33642E+00 6.26108E−02 H 7.39860E+00 −2.36017E+00 4.10022E+00 H 2.98978E+00 −6.08091E+00 1.55361E+00 H 5.09564E+00 −6.76700E+00 6.90904E+00 H 1.72762E+00 −3.93491E+00 −9.69470E−02  H 3.36497E−01 −3.76201E−01 −4.60527E+00  H 5.41281E+00  7.98900E−01 −1.62663E+00  H 7.06728E+00 −4.23845E+00 5.46018E+00 H 4.55996E+00 −7.53014E+00 4.23792E+00 H 3.62949E+00  8.19424E−01 −3.13418E+00  H 5.86305E−01 −2.24477E+00 −3.10313E+00  H 1.86094E+00 −8.26384E−01 7.49739E−01 C −1.00356E+00  −1.28950E+00 −6.61100E−02  C −5.76832E+00  −1.71557E+00 1.79697E+00 H −6.04342E+00  −6.59560E−01 1.64781E+00 H −5.82423E+00  −2.24011E+00 8.30105E−01 H −6.42701E+00  −2.18979E+00 2.53675E+00 C −1.12243E+00   6.23853E−01 −1.44684E+00  H −2.15896E+00   3.91882E−01 −1.73587E+00  H −4.23823E−01   2.16704E−01 −2.19151E+00  H −9.79883E−01   1.70694E+00 −1.33055E+00  H −3.60282E+00   2.91796E+00 3.03925E+00 H −2.20823E+00  −2.13990E+00 3.05318E+00 H −8.93141E−01  −2.91350E+00 1.26780E+00 C 2.08537E+00 −2.16708E+00 6.91106E+00 C 2.26348E+00 −2.51222E+00 5.56598E+00 C 2.63981E+00 −2.91624E−01 4.97878E+00 C 2.46333E+00  1.30664E−01 6.30110E+00 C 2.18153E+00 −8.21535E−01 7.29080E+00 H 1.87235E+00 −2.95228E+00 7.64210E+00 H 2.17463E+00 −3.54340E+00 5.21114E+00 H 2.90893E+00  4.04669E−01 4.18085E+00 H 2.55442E+00  1.19367E+00 6.54189E+00 H 2.04440E+00 −5.21451E−01 8.33474E+00

TABLE 12 xyz coordinates (in Angstroms) for structures in FIG. 53: exo isomer (3a). olefin exo (3a) C 1.51577E+00  7.97488E−01 −8.82461E−01  C 1.65083E+00 −5.40666E−01 −1.00826E+00  O −3.09073E+00  −1.55260E+00 −1.59129E+00  O −1.94766E+00  −2.49705E+00 1.39336E−01 O −2.78016E+00   7.48375E−01 5.42960E−01 O −2.87026E+00   2.06177E+00 −1.31714E+00  C 2.36582E−01  1.04923E+00 −9.27080E−02  C 4.61180E−01 −1.18911E+00 −3.06953E−01  C −7.84719E−01  −8.86527E−01 −1.22450E+00  C −9.50477E−01   6.84973E−01 −1.08638E+00  C 2.23659E−01 −1.82496E−01 8.46485E−01 H −7.38888E−01  −3.23640E−01 1.36189E+00 H 1.05525E+00 −1.64510E−01 1.57030E+00 H 5.61971E−01 −2.24993E+00 −4.06910E−02  H 2.39764E+00 −1.07960E+00 −1.59866E+00  H 2.12578E+00  1.57672E+00 −1.34817E+00  H 1.28653E−01  2.04266E+00 3.68740E−01 H −8.12345E−01   1.18112E+00 −2.05760E+00  H −5.62775E−01  −1.11765E+00 −2.28038E+00  C −2.07040E+00  −1.65545E+00 −9.22527E−01  C −2.28889E+00   1.12718E+00 −5.15068E−01  C −4.14787E+00   2.54558E+00 −8.42355E−01  H −4.47615E+00   3.27879E+00 −1.59109E+00  H −4.04053E+00   3.01760E+00 1.47209E−01 H −4.86590E+00   1.71414E+00 −7.67602E−01  C −3.15752E+00  −3.21777E+00 4.68403E−01 H −2.89484E+00  −3.84675E+00 1.32951E+00 H −3.48447E+00  −3.83494E+00 −3.83243E−01  H −3.95913E+00  −2.50991E+00 7.29858E−01 chelate exo (FIG. 52A) Ru 2.56860E+00 −2.69210E+00 2.06412E+00 C 1.71712E+00 −1.38818E+00 1.09789E+00 C 4.16879E+00 −3.00884E+00 9.24580E−01 N 5.07949E+00 −3.99113E+00 1.25101E+00 N 4.69444E+00 −2.33431E+00 −1.50400E−01  O −3.70287E+00  −3.32121E−01 3.34125E+00 O −1.60105E+00   5.45584E−01 3.45414E+00 O −1.18034E+00  −2.46084E+00 4.32821E+00 O 9.85226E−01 −2.52826E+00 3.68811E+00 Cl 3.82745E+00 −1.18276E+00 3.45556E+00 Cl 1.30221E+00 −4.61624E+00 1.31385E+00 C −1.97426E+00  −4.71675E−01 4.92621E−01 C 3.02548E−01 −9.36260E−01 1.32734E+00 C −2.07117E+00  −1.25883E+00 1.87653E+00 C −6.71240E−01  −1.89936E+00 2.04719E+00 C 6.33588E+00 −3.89832E+00 4.78774E−01 C 5.95486E+00 −2.93131E+00 −6.50263E−01  H 5.77275E+00 −3.44883E+00 −1.61196E+00  C 4.07301E+00 −1.33828E+00 −9.77281E−01  C −4.92769E−01  −6.35767E−01 3.15992E−02 C 4.94760E+00 −5.00970E+00 2.26456E+00 H 7.14652E+00 −3.49973E+00 1.11705E+00 C −2.96713E+00  −9.61022E−01 −5.26510E−01  C −3.90014E+00  −2.00817E−01 −1.12289E+00  H −1.25848E−01   2.55785E−01 −5.01239E−01  H −4.00949E−01  −1.49641E+00 −6.56774E−01  C −2.39291E+00  −2.62425E−01 2.98050E+00 H −2.16227E+00   5.99507E−01 6.85204E−01 H 3.62498E−01  7.05167E−04 1.92489E+00 H −4.00881E+00   8.64916E−01 −8.88531E−01  H −2.88950E+00  −2.02682E+00 −7.90472E−01  C 3.16347E+00 −1.73579E+00 −1.98741E+00  C 2.62384E+00 −7.38138E−01 −2.81927E+00  C 2.96850E+00  6.18830E−01 −2.67883E+00  C 3.87572E+00  9.73713E−01 −1.66389E+00  C 4.40309E+00 −6.26521E+00 1.88488E+00 C 4.29265E+00 −7.26631E+00 2.86321E+00 C 4.72808E+00 −7.06852E+00 4.18583E+00 C 5.34494E+00 −5.84750E+00 4.50199E+00 C 5.49266E+00 −4.81221E+00 3.55882E+00 C 3.99592E+00 −6.55196E+00 4.57943E−01 C 6.29227E+00 −3.58188E+00 3.92096E+00 C 4.54489E+00 −8.14583E+00 5.23285E+00 C 2.74485E+00 −3.18057E+00 −2.14536E+00  C 2.40073E+00  1.66599E+00 −3.61365E+00  H 3.68616E+00 −7.60448E+00 3.51661E−01 H 4.82964E+00 −6.37537E+00 −2.46861E−01  H 7.31028E+00 −3.63755E+00 3.48816E+00 H 5.81451E+00 −2.65412E+00 3.56860E+00 H 5.28079E+00 −8.04802E+00 6.04875E+00 H 4.64525E+00 −9.15515E+00 4.79792E+00 H 2.07500E+00 −3.29767E+00 −3.01298E+00  H 3.61172E+00 −3.84817E+00 −2.30078E+00  C 4.44606E+00  1.66230E−02 −8.05005E−01  C 5.39399E+00  4.30452E−01 2.97860E−01 H 5.51094E+00  1.52623E+00 3.18359E−01 H 5.02872E+00  9.69952E−02 1.28648E+00 H 1.40656E+00  1.37473E+00 −3.99249E+00  H 2.30472E+00  2.64480E+00 −3.11397E+00  H 6.71047E+00 −2.14718E+00 −8.21568E−01  H 6.64018E+00 −4.89316E+00 1.13555E−01 H 6.40928E+00 −3.50548E+00 5.01431E+00 H 3.15042E+00 −5.91413E+00 1.52697E−01 H 3.53893E+00 −8.08752E+00 5.68904E+00 H 2.21697E+00 −3.54906E+00 −1.24674E+00  H 3.05536E+00  1.81230E+00 −4.49341E+00  H 6.39990E+00 −8.63422E−03 1.62058E−01 H 5.74549E+00 −5.69359E+00 5.51144E+00 H 3.85853E+00 −8.23235E+00 2.57844E+00 H 4.14791E+00  2.02799E+00 −1.53134E+00  H 1.91294E+00 −1.03306E+00 −3.60097E+00  H 2.25684E+00 −7.67166E−01 3.62992E−01 C −2.02797E−01  −2.29985E+00 3.42112E+00 C −4.10171E+00   6.34315E−01 4.34106E+00 H −3.92595E+00   1.66007E+00 3.98017E+00 H −5.17280E+00   4.56231E−01 4.50500E+00 H −3.53278E+00   4.82413E−01 5.27172E+00 C −7.44689E−01  −2.91000E+00 5.63989E+00 H −6.85304E−02  −2.16603E+00 6.08703E+00 H −2.24450E−01  −3.87556E+00 5.55376E+00 H −1.66706E+00  −3.00859E+00 6.22635E+00 H −6.48244E−01  −2.85222E+00 1.47808E+00 H −2.86833E+00  −2.01686E+00 1.84040E+00 H −4.58976E+00  −6.12433E−01 −1.86683E+00  vacant exo (FIG. 52B) Ru 3.03309E+00 −2.71505E+00 2.35199E+00 C 1.93637E+00 −1.62589E+00 1.37604E+00 C 4.41760E+00 −3.23564E+00 1.08998E+00 N 5.39056E+00 −4.15238E+00 1.42484E+00 N 4.72092E+00 −2.76673E+00 −1.65666E−01  O −3.46966E+00  −2.22773E−01 2.16922E+00 O −2.45060E+00   8.20582E−01 3.92443E+00 O −1.45276E+00  −3.08562E+00 1.11275E+00 O −1.51262E+00  −2.30280E+00 3.25823E+00 Cl 4.30804E+00 −1.05355E+00 3.45488E+00 Cl 1.73531E+00 −4.68862E+00 2.42202E+00 C −1.07301E−01   1.39463E+00 2.38191E+00 C 9.13192E−01 −7.96028E−01 2.09389E+00 C −1.22217E+00   4.56240E−01 1.82628E+00 C −5.33121E−01  −9.28432E−01 1.50215E+00 C 6.49466E+00 −4.18581E+00 4.44094E−01 C 5.87612E+00 −3.47246E+00 −7.66579E−01  H 5.52847E+00 −4.18102E+00 −1.54276E+00  C 3.95573E+00 −1.88821E+00 −1.00516E+00  C 1.21616E+00  7.20711E−01 1.95138E+00 C 5.48991E+00 −4.91410E+00 2.64611E+00 H 7.37483E+00 −3.64731E+00 8.43822E−01 C −2.40998E−01   2.81945E+00 1.91316E+00 C −4.73695E−01   3.87548E+00 2.70962E+00 H 2.07804E+00  1.02538E+00 2.56473E+00 H 1.44929E+00  9.54390E−01 8.93980E−01 C −2.41163E+00   3.78804E−01 2.78701E+00 H −1.85073E−01   1.36937E+00 3.48341E+00 H 8.64946E−01 −1.04363E+00 3.17265E+00 H −5.91189E−01   3.75914E+00 3.79275E+00 H −1.37561E−01   2.97450E+00 8.27318E−01 C 2.92233E+00 −2.42028E+00 −1.81367E+00  C 2.23033E+00 −1.53948E+00 −2.66507E+00  C 2.54246E+00 −1.69173E−01 −2.73390E+00  C 3.57455E+00  3.21095E−01 −1.91237E+00  C 4.93884E+00 −6.22258E+00 2.66582E+00 C 5.05047E+00 −6.97102E+00 3.84749E+00 C 5.70412E+00 −6.47119E+00 4.98936E+00 C 6.30728E+00 −5.20657E+00 4.90544E+00 C 6.23832E+00 −4.41686E+00 3.74149E+00 C 4.28068E+00 −6.82167E+00 1.44421E+00 C 7.03248E+00 −3.13208E+00 3.66845E+00 C 5.75761E+00 −7.27948E+00 6.26737E+00 C 2.52582E+00 −3.87783E+00 −1.72554E+00  C 1.80605E+00  7.49250E−01 −3.68577E+00  H 4.03971E+00 −7.88280E+00 1.61943E+00 H 4.93851E+00 −6.76767E+00 5.57392E−01 H 8.05165E+00 −3.33241E+00 3.28353E+00 H 6.55645E+00 −2.37734E+00 3.02663E+00 H 6.58664E+00 −6.95452E+00 6.91785E+00 H 5.88307E+00 −8.35640E+00 6.06089E+00 H 1.69750E+00 −4.09718E+00 −2.41828E+00  H 3.36188E+00 −4.55321E+00 −1.98248E+00  C 4.29926E+00 −5.16210E−01 −1.04512E+00  C 5.39173E+00  4.06975E−02 −1.60749E−01  H 5.50983E+00  1.12419E+00 −3.23588E−01  H 5.16844E+00 −1.29390E−01 9.07746E−01 H 8.00557E−01  3.63957E−01 −3.92376E+00  H 1.69530E+00  1.76330E+00 −3.26566E+00  H 6.56050E+00 −2.75017E+00 −1.24045E+00  H 6.79010E+00 −5.22592E+00 2.30832E−01 H 7.14456E+00 −2.68534E+00 4.66941E+00 H 3.34385E+00 −6.29328E+00 1.20202E+00 H 4.82128E+00 −7.16640E+00 6.84467E+00 H 2.19850E+00 −4.14337E+00 −7.04106E−01  H 2.35258E+00  8.51984E−01 −4.64196E+00  H 6.36754E+00 −4.36796E−01 −3.65791E−01  H 6.86491E+00 −4.81933E+00 5.76680E+00 H 4.61488E+00 −7.97704E+00 3.87491E+00 H 3.82679E+00  1.38796E+00 −1.94614E+00  H 1.42113E+00 −1.93785E+00 −3.28911E+00  H 1.96508E+00 −1.50795E+00 2.79770E−01 C −1.22859E+00  −2.15548E+00 2.07629E+00 C −4.61758E+00  −4.27499E−01 3.02465E+00 H −4.97515E+00   5.32467E−01 3.42881E+00 H −5.38004E+00  −8.89125E−01 2.38258E+00 H −4.35014E+00  −1.09551E+00 3.85814E+00 C −1.98853E+00  −4.33891E+00 1.60374E+00 H −2.90513E+00  −4.16322E+00 2.18771E+00 H −1.23542E+00  −4.83834E+00 2.23257E+00 H −2.20174E+00  −4.93321E+00 7.05178E−01 H −4.60149E−01  −1.04603E+00 4.08351E−01 H −1.62214E+00   8.50851E−01 8.74967E−01 H −5.62342E−01   4.89060E+00 2.30853E+00 olefin adduct exo (FIG. 52C) Ru 2.73883E+00 −2.97367E+00 2.66814E+00 C 1.61472E+00 −1.96591E+00 1.62172E+00 C 4.25302E+00 −3.32244E+00 1.26000E+00 C 1.86029E+00 −2.47878E+00 4.79128E+00 C 9.76582E−01 −3.39680E+00 4.22805E+00 N 5.33434E+00 −4.09009E+00 1.58971E+00 N 4.39625E+00 −2.96305E+00 −4.76807E−02  O −3.23978E+00   6.18223E−01 2.42301E+00 O −1.60718E+00   1.08758E+00 3.94606E+00 O −2.00026E+00  −2.39358E+00 5.21051E−01 O −1.83272E+00  −2.08593E+00 2.77436E+00 O 1.30955E+00 −6.44831E+00 7.60410E+00 O −9.11108E−01  −6.12536E+00 7.20828E+00 O 3.46159E+00 −4.13098E+00 8.47917E+00 O 1.35729E+00 −3.95197E+00 9.34124E+00 Cl 4.09274E+00 −1.07523E+00 3.46091E+00 Cl 1.70669E+00 −5.02188E+00 1.71572E+00 C 2.86755E−01  1.62149E+00 1.81873E+00 C 8.10929E−01 −7.61679E−01 2.01750E+00 C −1.03071E+00   8.01222E−01 1.57362E+00 C −5.47821E−01  −6.63244E−01 1.26142E+00 C 6.33657E+00 −4.18752E+00 5.02673E−01 C 5.58857E+00 −3.57752E+00 −6.90392E−01  H 5.26594E+00 −4.33712E+00 −1.42493E+00  C 3.59308E+00 −2.09098E+00 −8.64089E−01  C 1.45136E+00  6.04079E−01 1.64659E+00 C 5.64870E+00 −4.66347E+00 2.87729E+00 H 7.24214E+00 −3.61682E+00 7.79026E−01 C 4.12054E−01  2.82049E+00 9.16802E−01 C 5.20347E−01  4.09288E+00 1.33370E+00 H 2.31969E+00  8.31733E−01 2.28184E+00 H 1.79292E+00  5.76042E−01 5.95665E−01 C −1.95105E+00   8.59082E−01 2.79486E+00 H 2.66036E−01  1.95503E+00 2.87066E+00 H 6.07136E−01 −7.63842E−01 3.10270E+00 H 5.18357E−01  4.34855E+00 2.39973E+00 H 4.21450E−01  2.60617E+00 −1.63492E−01  C 2.61886E+00 −2.64347E+00 −1.73243E+00  C 1.91558E+00 −1.76549E+00 −2.57857E+00  C 2.17639E+00 −3.84197E−01 −2.60906E+00  C 3.17503E+00  1.21133E−01 −1.75673E+00  C 5.30672E+00 −6.01867E+00 3.12800E+00 C 5.60182E+00 −6.55026E+00 4.39602E+00 C 6.23423E+00 −5.79220E+00 5.39770E+00 C 6.66267E+00 −4.49477E+00 5.06921E+00 C 6.41410E+00 −3.91800E+00 3.81117E+00 C 4.66021E+00 −6.88713E+00 2.07429E+00 C 7.04861E+00 −2.58897E+00 3.46852E+00 C 6.43404E+00 −6.34242E+00 6.79194E+00 C 2.32941E+00 −4.12680E+00 −1.76411E+00  C 1.43599E+00  5.26935E−01 −3.56533E+00  H 4.52504E+00 −7.91304E+00 2.45394E+00 H 5.28166E+00 −6.95048E+00 1.16133E+00 H 8.07932E+00 −2.74976E+00 3.09505E+00 H 6.47814E+00 −2.03154E+00 2.71349E+00 H 7.40846E+00 −6.03913E+00 7.21248E+00 H 6.37732E+00 −7.44363E+00 6.80720E+00 H 1.43951E+00 −4.33266E+00 −2.38103E+00  H 3.17045E+00 −4.69366E+00 −2.20673E+00  C 3.90218E+00 −7.08393E−01 −8.82940E−01  C 4.98774E+00 −1.31888E−01 −3.75449E−03  H 5.07951E+00  9.54702E−01 −1.63722E−01  H 4.78520E+00 −3.11501E−01 1.06781E+00 H 4.40104E−01  1.25740E−01 −3.81741E+00  H 1.30295E+00  1.53716E+00 −3.14230E+00  H 6.17068E+00 −2.80715E+00 −1.22176E+00  H 6.62474E+00 −5.23901E+00 3.42121E−01 H 7.11881E+00 −1.94658E+00 4.36051E+00 H 3.67347E+00 −6.49154E+00 1.77599E+00 H 5.65053E+00 −5.95503E+00 7.46932E+00 H 2.15365E+00 −4.53335E+00 −7.51676E−01  H 1.99160E+00  6.43898E−01 −4.51472E+00  H 5.97235E+00 −5.84443E−01 −2.26611E−01  H 7.21572E+00 −3.90823E+00 5.81272E+00 H 5.31404E+00 −7.58672E+00 4.60889E+00 H 3.40596E+00  1.19328E+00 −1.77512E+00  H 1.14752E+00 −2.18147E+00 −3.24189E+00  H 1.42329E+00 −2.31784E+00 5.88487E−01 C −1.52392E+00  −1.76895E+00 1.62970E+00 C −4.17057E+00   5.22539E−01 3.52678E+00 H −4.15285E+00   1.44454E+00 4.12830E+00 H −5.15583E+00   3.76548E−01 3.06373E+00 H −3.90611E+00  −3.35005E−01 4.16458E+00 C −2.88820E+00  −3.50609E+00 7.89319E−01 H −3.74108E+00  −3.17883E+00 1.40374E+00 H −2.34348E+00  −4.30503E+00 1.31578E+00 H −3.22435E+00  −3.85093E+00 −1.97375E−01  H −3.46816E−01  −7.28513E−01 1.77862E−01 H −1.60489E+00   1.17903E+00 7.11146E−01 H 6.16685E−01  4.92503E+00 6.28438E−01 C 2.63264E+00 −3.21522E+00 5.88243E+00 C 1.18587E+00 −4.70973E+00 4.97483E+00 C 5.55538E−01 −4.44164E+00 6.41242E+00 C 1.59579E+00 −3.42282E+00 7.04088E+00 C 2.69009E+00 −4.64770E+00 5.30699E+00 H 3.00944E+00 −5.39827E+00 6.04518E+00 H 3.32943E+00 −4.74328E+00 4.40966E+00 H 8.09292E−01 −5.61240E+00 4.47515E+00 H 4.74024E−02 −3.15724E+00 3.70600E+00 H 1.75670E+00 −1.39198E+00 4.79061E+00 H 3.57823E+00 −2.76138E+00 6.20410E+00 H 1.06448E+00 −2.48743E+00 7.29034E+00 H −4.40090E−01  −3.98327E+00 6.31815E+00 C 4.01746E−01 −5.75617E+00 7.15568E+00 C 2.27198E+00 −3.89301E+00 8.32812E+00 C 1.88686E+00 −4.44525E+00 1.05918E+01 H 1.04690E+00 −4.40741E+00 1.12989E+01 H 2.71801E+00 −3.81148E+00 1.09391E+01 H 2.24730E+00 −5.47856E+00 1.04673E+01 C −1.14700E+00  −7.40971E+00 7.82686E+00 H −2.23494E+00  −7.55512E+00 7.78793E+00 H −7.90457E−01  −7.40804E+00 8.86915E+00 H −6.26427E−01  −8.20807E+00 7.27428E+00 metallacyclobutane exo (FIG. 52D) Ru 2.79827E+00 −3.19662E+00 2.28691E+00 C 7.94338E−01 −2.74882E+00 2.25230E+00 C 4.56579E+00 −3.20713E+00 1.26221E+00 C 2.44357E+00 −3.88923E+00 4.09447E+00 C 9.85875E−01 −3.22192E+00 3.72425E+00 N 5.62308E+00 −3.92811E+00 1.72811E+00 N 4.93922E+00 −2.56671E+00 1.25610E−01 O −2.85137E+00   1.31721E+00 3.18429E+00 O −7.53097E−01   2.08650E+00 2.73441E+00 O −3.00529E+00  −2.00376E+00 3.61803E+00 O −1.23591E+00  −9.65080E−01 4.61854E+00 O −1.19478E+00  −6.52338E+00 6.07945E+00 O −1.99015E+00  −4.54913E+00 6.88658E+00 O 2.08302E+00 −7.41534E+00 6.53701E+00 O 1.00681E+00 −6.12041E+00 8.07575E+00 Cl 3.35953E+00 −1.09507E+00 3.39277E+00 Cl 2.21207E+00 −5.07201E+00 8.04586E−01 C −5.20535E−01   3.63870E−01 4.32099E−01 C 2.70152E−01 −1.34253E+00 2.02538E+00 C −1.63292E+00   1.36808E−01 1.51790E+00 C −1.27410E+00  −1.24445E+00 2.18677E+00 C 6.85464E+00 −3.68676E+00 9.36583E−01 C 6.31550E+00 −2.94175E+00 −2.94349E−01  H 6.26869E+00 −3.58292E+00 −1.19293E+00  C 4.19609E+00 −1.64310E+00 −7.00103E−01  C 4.49528E−01 −8.42903E−01 5.75134E−01 C 5.67312E+00 −4.78111E+00 2.89417E+00 H 7.56817E+00 −3.08023E+00 1.52406E+00 C −1.10752E+00   5.27347E−01 −9.45682E−01  C −1.14272E+00   1.67784E+00 −1.64108E+00  H 1.49275E+00 −5.65418E−01 3.57265E−01 H 1.69531E−01 −1.64979E+00 −1.30419E−01  C −1.65513E+00   1.28853E+00 2.52661E+00 H 1.31338E−02  1.28753E+00 7.13910E−01 H 7.50801E−01 −6.40301E−01 2.72726E+00 H −7.11503E−01   2.60298E+00 −1.24048E+00  H −1.55982E+00  −3.76347E−01 −1.38362E+00  C 3.49249E+00 −2.12524E+00 −1.83244E+00  C 2.86903E+00 −1.18218E+00 −2.66963E+00  C 2.95162E+00  2.01287E−01 −2.43645E+00  C 3.70300E+00  6.41847E−01 −1.33278E+00  C 5.49344E+00 −6.17816E+00 2.72310E+00 C 5.56699E+00 −6.99733E+00 3.86283E+00 C 5.83330E+00 −6.47840E+00 5.14333E+00 C 6.08358E+00 −5.10046E+00 5.25744E+00 C 6.02875E+00 −4.23141E+00 4.15081E+00 C 5.24578E+00 −6.79135E+00 1.36509E+00 C 6.36655E+00 −2.76853E+00 4.32275E+00 C 5.83142E+00 −7.38141E+00 6.35694E+00 C 3.43772E+00 −3.59411E+00 −2.18210E+00  C 2.25207E+00  1.18605E+00 −3.34590E+00  H 5.16210E+00 −7.88703E+00 1.44828E+00 H 6.07006E+00 −6.57466E+00 6.59921E−01 H 7.21277E+00 −2.46683E+00 3.67808E+00 H 5.51254E+00 −2.11396E+00 4.07083E+00 H 6.33524E+00 −6.90727E+00 7.21587E+00 H 6.33575E+00 −8.34106E+00 6.14869E+00 H 2.77777E+00 −3.75762E+00 −3.04963E+00  H 4.43712E+00 −3.98290E+00 −2.45542E+00  C 4.34618E+00 −2.53345E−01 −4.59216E−01  C 5.19618E+00  2.72528E−01 6.73687E−01 H 5.24636E+00  1.37282E+00 6.37511E−01 H 4.78458E+00 −2.49697E−02 1.65430E+00 H 2.18273E+00  8.03918E−01 −4.37865E+00  H 1.22079E+00  1.37302E+00 −2.99159E+00  H 6.89248E+00 −2.03664E+00 −5.41717E−01  H 7.33688E+00 −4.64498E+00 6.85940E−01 H 6.65992E+00 −2.56332E+00 5.36526E+00 H 4.31400E+00 −6.40268E+00 9.18719E−01 H 4.79371E+00 −7.61648E+00 6.65745E+00 H 3.06446E+00 −4.20313E+00 −1.34073E+00  H 2.77587E+00  2.15664E+00 −3.37122E+00  H 6.23241E+00 −1.10520E−01 6.21454E−01 H 6.34260E+00 −4.68172E+00 6.23755E+00 H 5.40893E+00 −8.07576E+00 3.74306E+00 H 3.81041E+00  1.71795E+00 −1.15110E+00  H 2.31785E+00 −1.54630E+00 −3.54509E+00  H 2.80635E−01 −3.50073E+00 1.62705E+00 C −1.79563E+00  −1.37633E+00 3.60823E+00 C −2.92777E+00   2.31063E+00 4.23424E+00 H −2.72449E+00   3.31467E+00 3.83088E+00 H −3.95376E+00   2.24551E+00 4.62113E+00 H −2.19532E+00   2.08101E+00 5.02363E+00 C −3.63661E+00  −2.07423E+00 4.91905E+00 H −3.76565E+00  −1.06203E+00 5.33287E+00 H −3.02799E+00  −2.67665E+00 5.61102E+00 H −4.61129E+00  −2.54786E+00 4.73915E+00 H −1.75149E+00  −2.03143E+00 1.57482E+00 H −2.64254E+00   6.86539E−02 1.07959E+00 H −1.61306E+00   1.74061E+00 −2.62819E+00  C 2.09935E+00 −5.30193E+00 4.56814E+00 C 5.78226E−02 −4.41214E+00 4.15301E+00 C 9.03988E−02 −4.46427E+00 5.72771E+00 C 1.52390E+00 −5.08325E+00 6.00416E+00 C 8.34819E−01 −5.68806E+00 3.78189E+00 H 3.50147E−01 −6.59308E+00 4.18045E+00 H 1.01465E+00 −5.79817E+00 2.70433E+00 H −9.62254E−01  −4.31604E+00 3.74727E+00 H 9.02787E−01 −2.32122E+00 4.35407E+00 H 2.98000E+00 −3.27472E+00 4.83754E+00 H 2.94145E+00 −6.00773E+00 4.54610E+00 H 2.11512E+00 −4.33788E+00 6.56850E+00 H −7.26832E−03  −3.45739E+00 6.16120E+00 C −1.06121E+00  −5.31609E+00 6.23895E+00 C 1.56347E+00 −6.35423E+00 6.85087E+00 C 9.70560E−01 −7.27462E+00 8.94564E+00 H 5.30666E−01 −6.91618E+00 9.88616E+00 H 1.98629E+00 −7.66542E+00 9.11409E+00 H 3.48469E−01 −8.06564E+00 8.49839E+00 C −3.12938E+00  −5.28962E+00 7.38469E+00 H −3.76176E+00  −4.54552E+00 7.88702E+00 H −2.80014E+00  −6.06460E+00 8.09405E+00 H −3.67214E+00  −5.77235E+00 6.55673E+00 pyridine adduct exo (FIG. 52E) Ru 2.96707E+00 −2.90511E+00 2.66262E+00 C 1.79328E+00 −1.91159E+00 1.66108E+00 C 4.36426E+00 −3.23431E+00 1.22604E+00 N 5.45116E+00 −4.02733E+00 1.51631E+00 N 4.57620E+00 −2.73406E+00 −3.19151E−02  N 1.79169E+00 −2.84941E+00 4.56149E+00 O −3.34125E+00   3.12413E−01 2.28019E+00 O −1.92025E+00   7.83741E−01 4.00223E+00 O −1.49726E+00  −2.73309E+00 4.90717E−01 O −1.84248E+00  −2.27069E+00 2.69812E+00 Cl 4.26023E+00 −1.01863E+00 3.49765E+00 Cl 1.82025E+00 −5.01210E+00 2.21354E+00 C 1.70198E−01  1.51007E+00 2.12939E+00 C 8.70924E−01 −8.27772E−01 2.13879E+00 C −1.06439E+00   6.40004E−01 1.70092E+00 C −4.71366E−01  −7.70140E−01 1.33947E+00 C 6.51559E+00 −3.96025E+00 4.91840E−01 C 5.79815E+00 −3.27227E+00 −6.77551E−01  H 5.52149E+00 −3.97872E+00 −1.48331E+00  C 3.69519E+00 −1.94734E+00 −8.49702E−01  C 1.41300E+00  6.08271E−01 1.89525E+00 C 5.67700E+00 −4.78498E+00 2.72371E+00 H 7.36952E+00 −3.36720E+00 8.69502E−01 C 2.44984E−01  2.82932E+00 1.40822E+00 C 2.23687E−01  4.03566E+00 1.99890E+00 H 2.25193E+00  8.47442E−01 2.56517E+00 H 1.77084E+00  6.95379E−01 8.51583E−01 C −2.11606E+00   5.88468E−01 2.81135E+00 H 6.99553E−02  1.69191E+00 3.21393E+00 H 6.49318E−01 −9.35827E−01 3.21432E+00 H 1.41845E−01  4.13872E+00 3.08715E+00 H 3.30640E−01  2.76963E+00 3.11692E−01 C 2.70365E+00 −2.59404E+00 −1.62767E+00  C 1.90639E+00 −1.80129E+00 −2.47384E+00  C 2.07928E+00 −4.08869E−01 −2.57410E+00  C 3.08014E+00  1.95429E−01 −1.79099E+00  C 5.26968E+00 −6.14634E+00 2.75301E+00 C 5.49888E+00 −6.88361E+00 3.92580E+00 C 6.14437E+00 −6.32719E+00 5.04531E+00 C 6.62278E+00 −5.01146E+00 4.94372E+00 C 6.42958E+00 −4.22798E+00 3.78916E+00 C 4.65502E+00 −6.81518E+00 1.54608E+00 C 7.11137E+00 −2.88254E+00 3.68471E+00 C 6.32973E+00 −7.13274E+00 6.31303E+00 C 2.46886E+00 −4.08475E+00 −1.52436E+00  C 1.23552E+00  4.13647E−01 −3.52506E+00  H 4.51220E+00 −7.89161E+00 1.73569E+00 H 5.30032E+00 −6.71426E+00 6.53857E−01 H 8.09785E+00 −2.99079E+00 3.19242E+00 H 6.51318E+00 −2.15018E+00 3.12349E+00 H 7.13505E+00 −6.71849E+00 6.94246E+00 H 6.57408E+00 −8.18616E+00 6.09141E+00 H 1.68560E+00 −4.40230E+00 −2.23176E+00  H 3.38126E+00 −4.66415E+00 −1.75441E+00  C 3.90359E+00 −5.49707E−01 −9.26810E−01  C 4.96768E+00  1.28853E−01 −9.43302E−02  H 4.93627E+00  1.22106E+00 −2.38631E−01  H 4.83669E+00 −8.78506E−02 9.80874E−01 H 2.71509E−01 −7.74136E−02 −3.73900E+00  H 1.02656E+00  1.41730E+00 −3.11699E+00  H 6.38673E+00 −2.45541E+00 −1.12646E+00  H 6.87922E+00 −4.97114E+00 2.43860E−01 H 7.29485E+00 −2.45943E+00 4.68587E+00 H 3.67346E+00 −6.37251E+00 1.30808E+00 H 5.40470E+00 −7.13599E+00 6.91909E+00 H 2.15400E+00 −4.37954E+00 −5.05425E−01  H 1.75175E+00  5.58623E−01 −4.49266E+00  H 5.98248E+00 −2.13219E−01 −3.71322E−01  H 7.18576E+00 −4.57843E+00 5.77976E+00 H 5.17074E+00 −7.92956E+00 3.95921E+00 H 3.23062E+00  1.28018E+00 −1.85453E+00  H 1.12792E+00 −2.29019E+00 −3.07199E+00  H 1.68977E+00 −2.13521E+00 5.82809E−01 C −1.35635E+00  −1.97423E+00 1.61120E+00 C −4.38504E+00   1.21720E−01 3.26164E+00 H −4.48802E+00   1.01531E+00 3.89701E+00 H −5.30162E+00  −5.26799E−02 2.68171E+00 H −4.14958E100   −7.49285E−01 3.89267E+00 C −2.20544E+00  −3.98128E+00 6.85446E−01 H −3.15753E+00  −3.80833E+00 1.20985E+00 H −1.58017E+00  −4.67513E+00 1.26970E+00 H −2.37699E+00  −4.37764E+00 −3.24206E−01  H −2.20666E−01  −7.68307E−01 2.64477E−01 H −1.56324E+00   1.04777E+00 8.05348E−01 H 2.88753E−01  4.96290E+00 1.41989E+00 C 5.11646E−01 −3.29350E+00 4.64466E+00 C −1.73730E−01  −3.40599E+00 5.85905E+00 C 4.84532E−01 −3.07008E+00 7.04886E+00 C 1.81069E+00 −2.62208E+00 6.97139E+00 C 2.42341E+00 −2.51976E+00 5.71815E+00 H 3.66767E−02 −3.56422E+00 3.70197E+00 H −1.21188E+00  −3.74828E+00 5.85494E+00 H −2.48725E−02  −3.15091E+00 8.01454E+00 H 2.37261E+00 −2.34353E+00 7.86754E+00 H 3.44382E+00 −2.14491E+00 5.60322E+00

REFERENCES CORRESPONDING TO EXAMPLE 2B

-   (1) Sveinbörnsson, B. R.; Weitekamp, R. A.; Miyake, G. M.; Xia, Y.;     Atwater, H. A.; Grubbs, R. H. Proc. Natl. Acad. Sci. U.S.A. 2012,     109, 14332-14336. -   (2) Lin, T.-P.; Chang, A. B.; Chen, H.-Y.; Liberman-Martin, A. L.;     Bates, C. M.; Voegtle, M. J.; Bauer, C. A.; Grubbs, R. H. J. Am.     Chem. Soc. 2017, 139, 3896-3903. -   (3) Bates, C. M.; Chang, A. B.; Momčilović, N.; Jones, S. C.;     Grubbs, R. H. Macromolecules 2015, 48, 4967-4973. -   (4) Love, J. A.; Morgan, J. P.; Trnka, T. M.; Grubbs, R. H. Angew.     Chem. Int. Ed. 2002, 41, 4035-4037. -   (5) Neese, F. Wiley Interdiscip. Rev.: Comput. Mol. Sci. 2017,     e1327.

Example 3A: Effects of Grafting Density on Block Polymer Self-Assembly: From Linear to Bottlebrush

Abstract: Grafting density is an important structural parameter that impacts the physical properties of architecturally complex polymers. In this example, the physical consequences of varying the grafting density (z) are contemplated in the context of block polymer self-assembly. Well-defined block polymers spanning the linear, comb, and bottlebrush regimes (0≤z≤1) are prepared via grafting-through ring-opening-metathesis polymerization (ROMP). ω-norbornenyl poly(D,L-lactide) (PLA) and polystyrene (PS) macromonomers are copolymerized with discrete co-monomers in different feed ratios, enabling precise control over both the grafting density and molecular weight. Small-angle X-ray scattering (SAXS) experiments demonstrate that these graft block polymers self-assemble into long-range-ordered lamellar structures. For seventeen series of block polymers with variable z, the scaling of the lamellar period with the total backbone degree of polymerization (d*˜N_(bb) ^(α)) are studied. The scaling exponent α monotonically decreases with decreasing z and exhibits an apparent transition at z≈0.2, suggesting significant changes in the chain conformations. Comparison of two block polymer systems, one that is strongly segregated for all z (System I) and one that experiences weak segregation at low z (System II), indicates that the observed trends are primarily motivated by the polymer architectures, not segregation effects. A model is contemplated in which the characteristic ratio (C_(∞)), a proxy for the backbone stiffness, scales with N_(bb) as a function of the grafting density: C_(∞)˜N_(bb) ^(f(z)). To the best of our knowledge, this report represents the first study of scaling behavior for the self-assembly of block polymers with variable grafting density. The scaling behavior disclosed herein provides valuable insights into conformational changes with grafting density, thus introducing new opportunities for block polymer and materials design.

Introduction: Block polymer self-assembly is a powerful process that connects molecular and materials design.¹⁻⁶ Due to their covalently linked yet chemically distinct blocks, block polymers provide access to a wide range of periodic structures by balancing competing entropic and enthalpic demands. Linear AB diblock polymers feature the simplest possible block connectivity and architecture, yet they still afford rich opportunities to tune structure and properties through the block volume fraction (f), binary block-block interaction parameter (χ), and total degree of polymerization (N). Due to this versatility, the self-assembly of block polymers has been exploited in many practical applications spanning all areas of science and technology.

Recent advances in polymer chemistry have enabled the precise synthesis of polymers with non-linear architectures.⁷⁻⁸ Introducing architectural complexity expands the opportunities for block polymer design. We recently reported the efficient synthesis of graft polymers with controlled grafting density (z), defined as the average number of polymer side chains per backbone repeat unit.⁹ In the present report, we study the effects of grafting density on the scaling of the lamellar period (d*) with the total backbone degree of polymerization (N_(bb)). The scaling of d* reflects steric demands and penalties to chain stretching, thus providing valuable insight into the physical consequences of varying polymer architectures. In addition, d* is an attractive parameter to study because it has an unambiguous physical definition (unlike potentially model-dependent parameters such as χ) and can be directly measured by scattering and electron microscopy.¹⁰

FIG. 36 (left side) illustrates the self-assembly of linear (z=0) diblock polymers into lamellar morphologies. For symmetric linear diblock polymers, arguments based on free energy demands accurately predict the scaling behavior (d*˜N_(bb) ^(α)). The scaling exponent α is ½ in the weak segregation limit (χN_(bb)≈10.5) and plateaus at ⅔ in the strong segregation limit (χN_(bb)>>10.5).¹¹⁻¹² The small scaling exponent is intrinsically related to the coil-like chain conformations. In contrast, reports of scaling behavior for block polymers with bottlebrush (z=1) and other complex, non-linear architectures are limited due to the synthetic challenges associated with (1) precisely controlling the architecture, molecular weight, and composition and (2) efficiently preparing multiple samples to study trends.

Bottlebrush polymers have recently emerged as an advanced class of non-linear architectures that manifest unique physical, mechanical, and dynamic properties.¹³⁻¹⁹ Like their linear analogues, bottlebrush diblock polymers can also access lamellar morphologies (FIG. 36). However, bottlebrush polymers display much larger scaling exponents (α=0.8-0.9),²⁰⁻²³ consistent with extended backbone conformations. Steric repulsion between the densely grafted side chains imparts a certain bending rigidity to the backbone, which can be modeled as a wormlike chain.²⁴⁻²⁷ The unique properties of bottlebrush polymers have been previously exploited for applications in photonics,²⁸⁻³² lithography,³³⁻³⁴ and surface coatings.³⁵ For example, the bottlebrush architecture minimizes chain entanglement and promotes rapid self-assembly to structures with ultra-large d*, enabling the fabrication of photonic materials that reflect visible and even infrared radiation. In contrast, such materials are generally inaccessible using linear and low-z analogues due to the ultra-high molecular weights required as well as the low entanglement molecular weights.

The effects of grafting density on the rheological properties of homopolymers have received tremendous interest.³⁶⁻⁴⁴ However, the impacts of grafting density on block polymer self-assembly have not been explored.⁴⁵⁻⁴⁸ Elucidating these physical principles is of fundamental importance and may also guide future materials design. With this mindset, we launched the first study on block polymers with systematically modified grafting densities (0≤z≤1) spanning the linear, comb, and bottlebrush regimes. The self-assembly of these unprecedented polymers is examined by small-angle X-ray scattering (SAXS), allowing determination of the scaling behavior. These studies reveal vital information on the backbone conformations, and the determined scaling laws allow prediction of lamellar periods of direct relevance to the development of nanomaterials.

Synthesis of block polymers with variable grafting densities (System I: Different diluents for each block). Ring-opening metathesis polymerization (ROMP) is a powerful strategy to synthesize well-defined bottlebrush polymers in a controlled and living manner.⁴⁹⁻⁵² We targeted poly(D,L-lactide)-b-polystyrene (PLA-b-PS) graft diblock polymers to permit comparisons with brush PLA-b-PS systems previously investigated in the context of self-assembly.²⁰⁻²⁴ In this example, polymerizations are carried out in CH₂Cl₂ at room temperature under an inert atmosphere. To vary the grafting density (FIG. 37), the first block is synthesized by copolymerizing a PLA macromonomer (M_(n)=3230 g/mol) with a discrete co-monomer (i.e., diluent), DME (endo,exo-norbornenyl dimethyl ester, M_(n)=210 g/mol). The grafting density (z) is precisely determined by the feed ratio according to Eq. 1:

$\begin{matrix} {z = \frac{\left\lbrack {PLA} \right\rbrack_{0}}{\left\lbrack {PLA} \right\rbrack_{0} + \lbrack{DME}\rbrack_{0}}} & (1) \end{matrix}$

After both co-monomers have been fully consumed (as verified by ¹H NMR), a mixture of a PS macromonomer (M_(n)=3990 g/mol) and another discrete diluent, DBE (endo,exo-norbornenyl di-n-butyl ester, M_(n)=294 g/mol), is introduced as the second block. The PS/DBE feed ratio is the same as the PLA/DME feed ratio in the first block. The determined reactivity ratios (block A: r_(PLA)=0.92, r_(DME)=1.11; block B: r_(PS)=0.80, r_(DBE)=1.16) suggest that the copolymerization is statistically random with minimal compositional drift.⁹ Monitoring the instantaneous monomer concentrations over time indicates that the macromonomer and diluent are incorporated at approximately equal rates in each block, consistent with uniform z throughout the entire block polymer. The backbone degrees of polymerization (n) for the first and second blocks are equal and determined by the ratio of the total monomer concentration to catalyst (G3) concentration (Eqs. 2-3):

$\begin{matrix} {n = {\frac{\left\lbrack {PLA} \right\rbrack_{0} + \lbrack{DME}\rbrack_{0}}{\left\lbrack {G3} \right\rbrack_{0}} = \frac{N_{bb}}{2}}} & (2) \\ {n = {\frac{\left\lbrack {PS} \right\rbrack_{0} + \left\lbrack {DBE} \right\rbrack_{0}}{\left\lbrack {G3} \right\rbrack_{0}} = \frac{N_{bb}}{2}}} & (3) \end{matrix}$

For System I, (see FIG. 38) nine different series with variable grafting densities (z=1.00, 0.75, 0.50, 0.35, 0.25, 0.20, 0.15, 0.05, and 0) are prepared. Each series includes five to seven block polymers with fixed composition and varying backbone lengths (N_(bb)=44-363, see Example 3B). To achieve consistent control over z, the targeted macromonomer/diluent feed ratios are verified by ¹H NMR prior to initiating the first block with G3. After reaching >99% conversion, the reaction mixtures are quenched by addition of excess ethyl vinyl ether. The block polymers are precipitated into methanol at −78° C., isolated by filtration, and dried under vacuum for >24 h. The first blocks and precipitated products are analyzed by NMR and size-exclusion chromatography (SEC), allowing determination of the molecular weights and therefore N_(bb). These analyses indicated that our methodology produced well-defined, monodisperse (Ð=1.01-1.18) graft block polymers.

Self-assembly and the lamellar period. With these graft block polymers in hand, we studied their self-assembly to lamellar morphologies. The isolated polymers are thermally annealed at 140° C. for 24 h under modest pressure (applied using binder clips). The samples are analyzed by synchrotron-source small-angle X-ray scattering (SAXS). Representative azimuthally averaged SAXS profiles corresponding to five samples with z=1 are shown in FIG. 38 (panel A). For all of the series investigated, the scattering patterns are consistent with well-ordered lamellar morphologies (see Example 3B and/or FIGS. 76 and 77). Scanning electron microscope (SEM) images obtained for selected block polymers with N_(bb)≈200 and z=1.00, 0.75, 0.50, or 0.25 also indicate long-range-ordered lamellar structures (FIG. 39, panels A, B, C, and D).

We note that varying the grafting density also changes the chemical composition within each block (i.e., by substituting PLA with DME and PS with DBE), potentially complicating the comparison of series with different z. In order to address the effects of varying the backbone chemistry, samples corresponding to loosely grafted individual A and B blocks—(PLA^(0.05)-r-DME^(0.95))₂₀₀ and (PS^(0.05)-r-DBE^(0.95))₂₀₀, respectively—are also studied. The samples are annealed under the same conditions as the graft block polymers. No evidence of microphase separation is observed by SAXS (see Example 3B and/or FIGS. 76 and 77), suggesting that each block behaves as a single component. In other words, the effective x in each block between the backbone and side chains can be regarded as negligible, and series with different z can be directly compared.

For all graft block polymers, the lamellar periods (d*) are determined by indexing the raw SAXS data. FIG. 38 (panel B) shows plots of d* versus N_(bb). The scaling relationships for each series are calculated using a least-square power-law fitting function in Igor. To gain additional insight into the scaling behavior, the determined scaling exponents a are plotted as a function of z (FIG. 38, panel C). For the z=1 series, the large magnitude of a (0.858) is consistent with previously reported values for symmetric PLA-b-PS bottlebrush block polymers (α=0.8-0.9).^(20-24,53) At the other extreme, the z=0 series exhibits an α value of 0.685, very close to the theoretical value (α=⅔) for strongly segregated symmetric linear diblock polymers.¹¹ The variable-z series (z=0.75, 0.50, 0.35, 0.25, 0.20, 0.15, 0.05) constitute intermediate regimes bridging the two extremes. Comparing all series, the scaling exponents decrease monotonically with decreasing z. However, while a modestly decreases from 0.858 (z=1.00) to 0.779 (z=0.20), it then sharply decreases with decreasing z to 0.685 (z=0). Collectively, these trends suggest changes in the backbone conformation with decreasing grafting density. Consistent with recent experimental and theoretical reports, at a certain critical z the conformational regime may transition from densely grafted brushes to loosely grafted brushes or combs.⁵⁴⁻⁵⁵ These changes significantly impact the physical properties of graft homopolymers, such as the plateau modulus and extensibility. However, the effects of grafting density on block polymer phase behavior are unexplored to date. In the final section of this report, we contemplate a model for the observed scaling behavior.

System II: Same diluent for both blocks. The potential consequences of changing χ within each block may be dismissed by considering individual A and B blocks. We note that varying the grafting density in System I may also affect the effective χ between blocks. Changing χ would influence d* and potentially complicate the interpretations of the observed scaling trends. For symmetric linear diblock polymers, d* exhibits a weak dependence on χ in the strongly segregated regime (d*˜χ¹¹⁶) and is independent of χ in the weakly segregated regime. In the mean-field Flory-Huggins lattice model, χ is determined by the number of nearest neighbor contacts per monomer. In our materials, since the number ratio of diluents to side chain monomers (i.e., either lactide or styrene repeats) is very small, the diluents are not expected to significantly affect χ. We anticipate that the large size disparity between macromonomers and diluents should make polymer architecture the primary factor responsible for the observed trends.

To examine this hypothesis, we prepared System II in which the same diluent (DBE) is employed to vary z in both blocks (FIG. 40). The lowest-z extreme (z=0) in System II is the homopolymer (DBE)_(n), which does not microphase separate. Macromonomers PLA (M_(n)=3030 g/mol) and PS (M_(n)=3800 g/mol) of similar molecular weights as those in System I are used. The determined reactivity ratios (r_(PLA)=1.04, r_(DBE)=0.89; r_(PS)=0.83, r_(DBE)=1.16) indicated random copolymerization within each block and therefore uniform grafting density. As for System I, polymers of general formula (PLA^(z)-r-DBE^(1-z))_(n)-b-(PS^(z)-r-DBE^(1-z))_(n) are prepared (N_(bb)=2n=82-533; z=0.75, 0.50, 0.35, 0.25, 0.15, 0.12, 0.06, 0.05). The isolated monodisperse (

=1.02-1.19) copolymers are characterized by NMR and SEC.

The samples are thermally annealed under the same conditions as System I. All of the polymers in System II self-assembled into well-ordered lamellae as evidenced by SAXS (see Example 3B and/or FIGS. 76 and 77). (Azimuthally averaged 1 D SAXS plots obtained for the z=0.75 series are shown in FIG. 41, panel A, as representative examples.) FIG. 41, panel B, shows the power-law fitting plots (d* versus N_(bb)) for each series. The a values in System II are uniformly smaller compared to their counterparts of the same grafting density in System I. This observation could be attributed to the larger changes in χ between blocks upon decreasing z. The z=0.05 series displays an α value of 0.515, approaching the theoretical value in the weak segregation limit (α=½).¹⁻¹² Comparing FIGS. 38, panel C, and 41, panel C, suggests that the different d* and a values are likely due to different changes in χ. The linear diblock polymer (DME)_(n)-b-(DBE)_(n), which is exactly the z=0 series in System I, is itself strongly segregated, whereas the z=0 series in System II is the homopolymer (DBE)_(n). However, we note that the transition between regions of shallow and steep decreases in α with decreasing z occur at nearly the same z in both systems (z≈0.2), suggesting that such transition is intrinsically related to polymer architecture rather than segregation strengths.

Significance of the determined scaling relationships. Present example appears to be the first to study how grafting density affects the scaling of the lamellar period with the total backbone degree of polymerization. Understanding these scaling relationships expands the parameter space for materials design. Materials with controlled length scales are desired for many applications. For example, ultra-large d* values are required by photonic crystals in order to access the visible spectrum. In general, linear polymers are prohibitively challenging to synthesize and process at sufficiently high molecular weights. Meanwhile, bottlebrush block polymers are attractive building blocks due to their reduced chain entanglement and steep increase in d* with molecular weight. However, synthesizing fully grafted, ultra-high-molecular-weight bottlebrush block polymers can be challenging and expensive. In grafting-through strategies, the concentrations of reactive chain ends are low, and the side chains are typically synthesized by costly metal-mediated controlled polymerizations. Through grafting-through copolymerization however, N_(bb) can be readily increased by introducing small-molecule diluents that can be synthesized on large scales from readily available precursors.

The ability to simultaneously tune the grafting density and backbone length provides an additional tool for designing materials with desired length scales. For example, according to the determined scaling relationship for fully grafted bottlebrush block polymers (z=1.00, d*=1.033×N_(bb) ^(0.858)), a polymer with N_(bb)=100 should self-assemble to lamellae with d*=53.6 nm. In System I, a 50% grafted block polymer (z=0.50, d*=0.926×N_(bb) ^(0.815)) with the same number of side chains has N_(bb)=200 and should self-assemble to lamellae with d*=69.5 nm. In other words, decreasing the grafting density (z=1.00 to 0.50) while maintaining the same number of side chains results in a large increase in d* (30%) at the expense of a small increase in total molecular weight (7%). The modest increase in M is highly advantageous for processing these materials since the zero-shear viscosity scales with M (η₀˜M^(C)). Below the onset of entanglements at a critical molecular weight M_(c), α=1, whereas above M_(c), α=3.4. The influence of grafting density on rheological properties are also contemplated.

We further highlight the significance of grafting density effects on the scaling of the lamellar period by predicting the required N_(bb) to reach an arbitrary value of d*=200 nm (FIG. 42, panels A and B). Such a large d* is desired for photonic applications. At the same z, N_(bb) required to reach d*=200 is larger for block polymers in System II than in System I as a result of differences in segregation strengths. In both systems, the predicted N_(bb) values exponentially increase with decreasing z below the observed transition (z<0.20). In the linear block polymer limit (z=0, System I), the required N to reach d*=200 nm is close to 4000. Such high-molecular-weight linear polymers are extremely challenging to synthesize, and as a result there are very few examples of linear block polymers that can self-assemble to visible-light-reflecting photonic crystals.⁵⁶ Existing examples are typically limited by low conversion and inability to process the materials from the melt. In contrast, a 50% grafted block polymer may require N_(bb)≈730. Manipulating the grafting density through copolymerization therefore constitutes a promising strategy to overcome limitations associated with both synthesis and processing.

Interpretation of the scaling trends. We derive a model in order to relate the observed changes in a with grafting density (z) to the conformations of the graft polymer backbone and side chains. Key experimental results to capture include (1) the monotonic decrease in α with z (FIGS. 38, panel C, and 41, panel C), (2) the apparent transition between shallow and steep decreases in a at a critical z_(c)=0.2, and (3) potential segregation effects that emerge at low z. Comparison of two systems—one in which all series (z 0) are in the strongly segregated limit (SSL) (System I) and one that bridges the strongly and weakly segregated limits (WSL) (System II)—suggests that architecture effects, not segregation effects, are primarily responsible for the observed trends. We begin by framing our results in the context of existing theory for the self-assembly of diblock polymers, then propose a functional form for the observed relationship between z and d*, i.e., d*˜N_(bb) ^(f(z)). We note that, in part due to the long-standing challenges associated with synthesizing well-defined graft polymers, there is not currently a theoretical or experimental consensus detailing the effects of grafting density on block polymer self-assembly.

The scaling of the lamellar period (d*) is well-understood in the case of symmetric linear diblock polymers.^(11-12,57) The magnitude of d* is determined by the balance between the elastic energy (F_(stretch)), which resists chain stretching, and the interfacial energy (F_(int)), which resists expansion of block junctions along the domain interfaces. The stretching free energy per polymer chain is inversely proportional to the mean-square end-to-end distance, (R²):

$\begin{matrix} {\frac{F_{stretch}}{kT}\text{∼}\frac{d^{2}}{\left\langle R^{2} \right\rangle}} & (4) \end{matrix}$

When the chain is flexible, the mean-square end-to-end distance is given by

R

=a₀ ²N_(bb), where a₀ is the statistical segment length and N_(bb) is the backbone degree of polymerization. (Note that in the case of linear polymers, N_(bb) is identical to the total degree of polymerization.) The interfacial energy per polymer chain is

$\begin{matrix} {\frac{F_{int}}{kT}\text{∼}\gamma A} & (5) \end{matrix}$

where γ is the surface tension and A is the area per chain. These parameters can be approximated by γ=χ^(1/2)a₀ ⁻² and A˜N_(bb)a₀ ³/d*, leading to the following expression:

$\begin{matrix} {\frac{F_{int}}{kT}\text{∼}\frac{N_{bb}a_{0}\chi^{\frac{1}{2}}}{d^{*}}} & (6) \end{matrix}$

In the SSL, the elastic energy and interfacial energy are balanced (F_(stretch)=F_(int)), and thus we obtain

d*≈χ ^(1/6) N ^(1/3)[

R ²

]^(1/3) ˜a ₀χ^(1/6) N _(bb) ^(2/3)  (7)

In the WSL, the chains do not significantly stretch at the interface because χ is small, and thus F_(int) is effectively negligible. Therefore,

$\begin{matrix} {d^{*}{\text{∼}\left\lbrack \left\langle R^{2} \right\rangle \right\rbrack}^{\frac{1}{2}}\text{∼}a_{0}N_{bb}^{\frac{1}{2}}} & (8) \end{matrix}$

Collectively, following Eqs. 7 and 8, the d* scaling relationship for diblock polymers has the general form

d*˜a ₀ N _(bb) ^(α)  (9)

For flexible linear diblock polymers, typically ½≤α≤⅔. In contrast, when the polymer is semi-flexible, the same general form applies but the scaling exponent α is larger.⁵⁸⁻⁵⁹ Bottlebrush diblock polymers typically exhibit α close to 0.9, reflecting the extended backbone conformations due to the sterically demanding architecture.^(22-23,31) We note that, in the limit of extremely long backbones, when the persistence length and cross-sectional diameter are much shorter than the contour length of the brush, the chain should become flexible and α should approach ⅔.^(24,60) In the current study however, the graft polymers exclusively reside in the regime in which the backbone persistence length (l_(p)) is not negligible compared to N_(bb).

For non-flexible polymers, the mean-square end-to-end distance can be written as

R ²

a ₀ ² C _(∞) N _(bb)  (10)

by adopting Flory's characteristic ratio, C_(∞)=2l_(p)/a₀. Therefore,

R ²

=2a ₀ l _(p) N _(bb)  (11)

For bottlebrush polymers, l_(p) is a function of the side chain degree of polymerization (N_(sc)) and z.^(55,61) l_(p) is also anticipated to be a function of N_(bb) by theory and simulations,^(54,62) but the functional form of this relationship is currently a matter of some debate. We may assume that C_(∞) is a function of N_(bb) and z in order to study how the backbone stiffness affects d*.

Two boundary conditions of this function are known. First, when z=0, C_(∞)=1 by definition since the backbone is identical to a flexible linear polymer. Second, in the opposite limit, when z=1, C_(∞) should approach N_(bb). To satisfy these conditions, we write the following power function describing the relationship between C_(∞) and N_(bb):

C _(∞) =N _(bb) ^(mz+b)  (12)

We now insert Eq. 12 into Eq. 10, then rewrite the expressions for d* in the SSL (Eq. 7) and WSL (Eq. 8) in terms of C_(∞):

$\begin{matrix} {d^{*}\text{∼}\left\{ \begin{matrix} {a_{0}\chi^{\frac{1}{6}}C_{\infty}^{\frac{1}{3}}N_{bb}^{\frac{2}{3}}} & {SSL} \\ {a_{0}C_{\infty}^{\frac{1}{2}}N_{bb}^{\frac{1}{2}}} & {WSL} \end{matrix} \right.} & (13) \end{matrix}$

Therefore, the experimentally observed scaling exponents a can be written as follows:

$\begin{matrix} {\alpha = \left\{ \begin{matrix} \frac{{mz} + b + 2}{3} & {SSL} \\ \frac{{mz} + b + 1}{2} & {WSL} \end{matrix} \right.} & (14) \end{matrix}$

We now apply Eq. 14 to Systems I and II in order to evaluate how C_(∞), as a proxy for the backbone stiffness, changes with z. In System I, different diluents (DME and DBE) are used to vary z in each block. The linear diblock polymer DME-b-DBE exhibits α=0.688≈⅔. This result suggests that, even in the z=0 limit, the block polymers in System I are strongly segregated. Since a may just increase with z, all series in System I are expected to be in the SSL. FIG. 43, panel A, shows the lines of best fit for experimentally determined values of α and z. Two regions are identified, diverging at a critical grafting density z_(c,I): (1) when z<0.2, α steeply decreases with decreasing z; (2) when z>0.2, α slightly decreases with decreasing z. In the first region, α=0.46z+0.68; in the second region, α=0.091z+0.77. The lines of best fit intersect at z_(c,I)=0.23. We obtain the following expressions for C_(∞).

$\begin{matrix} {C_{\infty} = \left\{ \begin{matrix} N_{bb}^{1.39z} & {z < {{0.2}3}} \\ N_{bb}^{{0.27z} + {{0.3}0}} & {z > {{0.2}3}} \end{matrix} \right.} & (15) \end{matrix}$

Introducing Eq. 15 into Eq. 10 enables calculations of the normalized root-mean-square end-to-end distances (√{square root over (

R²

)}/a₀) as a function of z (FIG. 43, panel A). The transition in √{square root over (

R²

)}/a₀ occurs near z_(c,I): z=0.27.

Unlike System I, System II uses the same diluent (DBE) for both blocks. The z=0 limit constitutes a linear homopolymer rather than a diblock polymer, and therefore the segregation behavior and chain stretching at the domain interface differ between Systems I and II. Applying the same analysis for System II, when the grafting density is low (z<0.2) we obtain α=1.44z+0.50 (FIG. 43, panel B). In this region, the block polymers experience intermediate to weak segregation (α<⅔). Reflecting the boundary condition C_(∞)=1 at z=0, the y-intercept is fixed at ½. Therefore, applying Eq. 14 in the WSL, m=2.87 and b=0. By comparison to System I and literature results, we expect the series to experience strong segregation at a certain z. We may assume that, at least when z>0.2, the block polymers are in the SSL. Therefore, α=0.15z+0.71 suggests m=0.46, b=0.12. The lines of best fit intersect at z_(c,II)=0.16. From these results, for System II we obtain the following expression for C″:

$\begin{matrix} {C_{\infty} = \left\{ \begin{matrix} N_{bb}^{2.87z} & {z < {{0.1}6}} \\ N_{bb}^{{0.46z} + {{0.1}2}} & {z > {{0.1}6}} \end{matrix} \right.} & (16) \end{matrix}$

FIG. 43B (bottom) shows the values of √{square root over (

R²

)}/a₀ calculated for System II per Eq. 16. Surprisingly, √{square root over (

R²

)}/a₀ exhibits an apparent transition at z=0.05, much lower

than the value z_(c,II)=0.16 identified by fitting the experimental data (FIG. 43B, top). In contrast, for System I the transitions in α and √{square root over (

R²

)}/a₀ occur at approximately the same z (FIG. 43A). Since √{square root over (

R²

)}/a₀ is obtained from fitting α in two regions (diverging at a critical z_(c) and assuming either weak or strong segregation), the transitions should occur at the same z if the proposed model accurately describes the entire z range. The observed mismatch suggests that our model does not reflect all factors affecting d* in the transition region. The preceding discussions have focused on the backbone stiffness. However, the potential contributions of χ and side chain conformations is also contemplated.

FIGS. 43A-43B indicate that changes in C, alone do not fully capture the scaling of the lamellar period. Changes in the segregation strength that emerge with decreasing z are likely also significant. In System I, the diluents are different and the polymers are already stretched at z=0 (inferred based on α>⅔). Since the backbones are already stretched, increasing z may not significantly affect χ between the two grafted blocks or backbone stretching. A high grafting density (large z_(c)) may be required to further stretch the chains. In System II however, the z=0 limit describes linear homopolymers, which are expected to adopt unperturbed conformations. Therefore, the onset of backbone and side chain stretching should occur at a lower z_(c). The effects of segregation, as well as the precise location of the transition between SSL and WSL with z, are important factors to consider.

To conclude our interpretation of the scaling relationships, we address the potential role of the side chains in the experimentally observed transition at z_(c)≈0.20. Our analysis is consistent with C, changing abruptly at z_(c). We note that, for System I, all series (0≤z≤1) are in the SSL. Steric repulsion between the side chains is expected to be the primary factor responsible for increasing C″. The location of the transition z_(c) is therefore expected to be related to the onset of side chain overlap. The radius of gyration of a side chain is

R _(g,sc) =a _(sc)(N _(sc)/6)^(1/2)  (17)

where a_(sc) is the statistical segment length of the side chain. In order for the side chains to retain their unperturbed conformations, the contour length of a section of backbone separating adjacent side chains (L_(g)) should be larger than 2R_(g,sc). As z increases, the side chains are expected to stretch to accommodate tethering at shorter L_(g).⁶¹

Consistent with a convention employed by previous theories and experiments for bottlebrush polymers,²⁴ we assume that the contour length per polynorbornene backbone segment is constant (L_(s)=0.62 nm). The number of backbone segments between adjacent grafting points (inclusive) is provided by 1/z, and L_(g) follows:

$\begin{matrix} {L_{g} = \frac{L_{s}}{z}} & (18) \end{matrix}$

When L_(g)>2R_(g,sc), the backbone is expected to behave as a flexible Gaussian chain. When L_(g)<2R_(g,sc), the backbone is expected to stretch, ultimately leading to wormlike chain conformations at sufficiently high z. The stiffness of the brush is expected to increase when two neighboring grafts contact each other in the limiting range of the torsional angle. We define z_(s) as the grafting density at the onset of backbone stretching due to torsional limitations (L_(g)=2R_(g,sc)):

$\begin{matrix} {Z_{s} \equiv \frac{L_{s}}{2{a_{sc}\left( {N_{sc}/6} \right)}^{\frac{1}{2}}}} & (19) \end{matrix}$

As an approximation, we estimate that the transition in the brush conformation responsible for the transition in a occurs when z=z_(s). We note that stretching of the side chains at z>z_(s) may not permit this simple approximation, since stretching of the graft polymer backbone and side chains should compete to balance conformational entropy. We further assume N_(sc)=36 and L_(s)≈a_(sc), producing z_(s)=0.20. For both Systems I and II, the experimentally observed transition in a occurs at z_(c) z_(s) (z_(c,I)=0.23, z_(c,II)=0.16). This observation suggests that the steep increase in a at small z is mainly due to the stretching of the backbone, whereas the modest increase in a at high z is mainly due to the increasing torsional angle demanded by decreasing L_(g).

These results collectively suggest that changes in the end-to-end distance

R²

are primarily responsible for the increase in α with increasing z.

R²

may increase due to a combination of backbone stretching, torsional limitations, and χ effects

R²

exhibits two regimes in terms of z dependence, corresponding to a transition between loose and densely grafted brushes.⁶³⁻⁶⁴ In our model, we propose functional forms for (1) the relationship between backbone stiffness and backbone length (C_(∞)˜N_(bb) ^(f(z))) and (2) the relationship between the lamellar period scaling exponent and grafting density (α˜mz+b). We anticipate that the materials and framework outlined herein should stimulate additional theories and experiments.

CONCLUSIONS: The self-assembly of block polymers enables diverse practical applications. We herein provide the first experimental study that quantitatively correlates grafting density with scaling of the lamellar period. Through the analyses of well-defined graft block polymer assemblies, we show that the scaling exponent undergoes a sharp transition at z≈0.20. The observed transition is attributed to different conformational regimes dictated by backbone chain conformations. We contemplate that the determined scaling relationships for various grafting density series may be exploited to guide future material design.

MATERIALS AND METHODS: General considerations. Norbornene macromonomers PS⁶⁵ and PLA²² are prepared according to previously reported precedures. Norbornene diluents DME⁶⁶ and DBE⁶⁷ are prepared by Diels-Alder reactions according to previously reported procedures. Grubbs' second-generation catalyst [(H₂IMes)(PCy₃)(Cl)₂Ru═CHPh] is provided by Materia, and G3 is prepared according to the reported precedure.⁶⁸ CH₂Cl₂ is dried by passing through an activated alumina column. Deuterated solvents are purchased from Cambridge Isotopes Laboratories, Inc. and used as received.

NMR, SEC, SEM, and SAXS characterizations. Ambient temperature NMR spectra are recorded on a Varian 300 MHz, 400 MHz, or 500 MHz NMR spectrometer. Chemical shifts (8) are given in ppm and referenced against residual solvent signals (¹H, ¹³C). SEC data are collected using two Agilent PLgel MIXED-B 300×7.5 mm columns with 10 μm beads, connected to an Agilent 1260 Series pump, a Wyatt 18-angle DAWN HELEOS light scattering detector, and Optilab rEX differential refractive index detector. The mobile phase is THF. Online determination of dn/dc assumed 100% mass elution under the peak of interest. (Further details about SEC can be found in FIGS. 53-57 and 59-75) Samples are prepared for SEM by fracturing films supported on glass to expose a cross-section, staining over ruthenium tetroxide vapors for 5 minutes, then coating with 5 nm Pd/Pt. SEM images are taken on a ZEISS 1550 VP Field Emission SEM. SAXS data are collected at beamline 12-ID at Argonne National Laboratory's Advanced Photon Source. The samples are probed using 12 keV (1.033 Å) X-rays, and the sample-to-detector distance is calibrated using a silver behenate standard. The beam is collimated using two sets of slits and a pinhole is used to remove parasitic scattering. The beamwidth is approximately 200-300 μm horizontally and 50 μm vertically.

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Example 3B3: Effects of Grafting Density on Block Polymer Self-Assembly

TABLE 13 Total molecular weights (M_(n)), total backbone degrees of polymerization (N_(bb)), and lamellar periods (d*) for (PLA^(x)-r-DME^(1−x))_(n)-b-(PS^(x)-r-DBE^(1−x))_(n) graft block polymers (System I). z Sample ID M_(n) (kDa) N_(bb) d* (nm) 1.00 A1 158 44 27.5 A2 304 84 46.0 A3 465 129 65.8 A4 596 165 82.0 A5 718 199 97.5 0.75 B1 234 84 40.3 B2 361 130 58.2 B3 467 168 72.5 B4 606 219 89.5 0.50 C1 166 86 35.0 C2 243 126 47.6 C3 315 163 58.7 C4 400 207 71.5 0.35 D1 124 87 29.7 D2 181 127 40.5 D3 238 167 50.5 D4 301 211 62.0 D5 369 258 71.5 D6 430 301 81.0 0.25 E1 98.8 90 27.9 E2 146 134 36.7 E3 167 153 41.5 E4 200 183 47.0 E5 216 197 51.5 E6 244 223 55.5 E7 286 262 63.5 0.20 F1 119 128 33.6 F2 153 166 42.5 F3 195 211 50.0 F4 216 234 55.0 F5 230 249 57.5 F6 248 268 61.0 F7 294 318 69.0 0.15 G1 163 216 43.6 G2 178 235 46.6 G3 189 250 50.3 G4 216 286 54.0 G5 232 307 57.0 G6 246 325 60.0 0.05 H1 91.7 218 33.5 H2 103 246 37.0 H3 111 264 39.0 H4 124 294 41.2 H5 129 308 43.0 H6 142 339 46.2 0.00 I1 46.5 184 26.3 I2 55.4 219 29.5 I3 62.7 249 32.1 I4 72.4 287 35.4 I5 82.3 326 38.9 I6 91.5 363 41.6

TABLE 14 Total molecular weights (M_(n)), total backbone degrees of polymerization (N_(bb)), and lamellar periods (d*) for (PLA^(z)-r-DBE^(1−z))_(n)-b-(PS^(z)-r-DBE^(1−z))_(n) graft block polymers (System II). z Sample ID M_(n) (kDa) N_(bb) d* (nm) 0.75 J1 116 44 23.5 J2 215 82 36.8 J3 330 125 52.4 J4 402 152 62.6 J5 521 198 76.0 J6 649 246 92.0 0.50 K1 249 135 43.0 K2 322 174 52.8 K3 396 213 62.2 K4 472 254 70.2 K5 529 285 78.0 K6 603 325 85.7 0.35 L1 241 174 46.5 L2 307 221 55.0 L3 364 263 62.5 L4 436 314 71.0 L5 472 341 78.0 L6 538 388 85.0 0.25 M1 232 216 42.6 M2 277 258 48.2 M3 335 312 54.1 M4 384 358 61.9 M5 406 378 64.0 M6 472 439 71.4 0.15 N1 98.5 129 24.0 N2 161 212 32.8 N3 193 253 37.5 N4 213 279 41.5 N5 251 329 46.6 N6 299 392 51.8 0.12 O1 150 224 32.8 O2 183 274 36.5 O3 221 330 42.0 O4 248 370 44.3 O5 274 409 49.0 O6 302 451 52.5 0.06 P1 156 324 30.3 P2 177 367 31.8 P3 199 413 34.2 P4 226 469 37.3 P5 257 533 40.4 0.05 Q1 152 337 27.2 Q2 169 376 28.5 Q3 184 408 30.0 Q4 203 451 31.5

TABLE 15 Lamellar scaling laws (d* = b × N_(bb) ^(α)) obtained for System I using the least-square power-law fitting function in Igor. z b □ 1.00 1.033 0.858 0.75 0.999 0.835 0.50 0.926 0.815 0.35 0.838 0.801 0.25 0.788 0.788 0.20 0.781 0.779 0.15 0.778 0.751 0.05 0.750 0.707 0.00 0.737 0.685

TABLE 16 Lamellar scaling laws (d* = b × N_(bb) ^(α)) obtained for System II using the least-square power-law fitting function in Igor. z b □ 0.75 1.049 0.812 0.50 0.949 0.779 0.35 0.872 0.768 0.25 0.787 0.741 0.15 0.726 0.716 0.12 0.778 0.688 0.06 0.924 0.601 0.05 1.356 0.515

STATEMENTS REGARDING INCORPORATION BY REFERENCE AND VARIATIONS

All references cited throughout this application, for example patent documents including issued or granted patents or equivalents; patent application publications; and non-patent literature documents or other source material; are hereby incorporated by reference herein in their entireties, as though individually incorporated by reference, to the extent each reference is at least partially not inconsistent with the disclosure in this application (for example, a reference that is partially inconsistent is incorporated by reference except for the partially inconsistent portion of the reference).

The terms and expressions which have been employed herein are used as terms of description and not of limitation, and there is no intention in the use of such terms and expressions of excluding any equivalents of the features shown and described or portions thereof, but it is recognized that various modifications are possible within the scope of the invention claimed. Thus, it should be understood that although the present invention has been specifically disclosed by preferred embodiments, exemplary embodiments and optional features, modification and variation of the concepts herein disclosed may be resorted to by those skilled in the art, and that such modifications and variations are considered to be within the scope of this invention as defined by the appended claims. The specific embodiments provided herein are examples of useful embodiments of the present invention and it will be apparent to one skilled in the art that the present invention may be carried out using a large number of variations of the devices, device components, methods steps set forth in the present description. As will be obvious to one of skill in the art, methods and devices useful for the present methods can include a large number of optional composition and processing elements and steps.

Where used, a bond represented by “

” (a squiggly or wavy line) refers to a bond having any angle or geometry, such as in the case of a chemical species exhibiting stereochemistry such as chirality. For example, the compound of formula (FX90):

may correspond to one or more compounds, such as those having the formulas (FX90a), (FX90b), (FX90c), and (FX90d):

It must also be noted that a bond represented as a non-wavy or non-squiggly line(s), such as a “

”, may exhibit more than one stereochemical configuration, such as chirality.

When a group of substituents is disclosed herein, it is understood that all individual members of that group and all subgroups are disclosed separately. When a Markush group or other grouping is used herein, all individual members of the group and all combinations and subcombinations possible of the group are intended to be individually included in the disclosure. Additionally, unless otherwise specified, all isotopic variants of compounds disclosed herein are intended to be encompassed by the disclosure. For example, it will be understood that any one or more hydrogens in a molecule disclosed can be replaced with deuterium or tritium. Isotopic variants of a molecule are generally useful as standards in assays for the molecule and in chemical and biological research related to the molecule or its use. Methods for making such isotopic variants are known in the art. Specific names of compounds are intended to be exemplary, as it is known that one of ordinary skill in the art can name the same compounds differently.

It must be noted that as used herein and in the appended claims, the singular forms “a”, “an”, and “the” include plural reference unless the context clearly dictates otherwise. Thus, for example, reference to “a cell” includes a plurality of such cells and equivalents thereof known to those skilled in the art, and so forth. As well, the terms “a” (or “an”), “one or more” and “at least one” can be used interchangeably herein. It is also to be noted that the terms “comprising”, “including”, and “having” can be used interchangeably. The expression “of any of claims XX-YY” (wherein XX and YY refer to claim numbers) is intended to provide a multiple dependent claim in the alternative form, and in some embodiments is interchangeable with the expression “as in any one of claims XX-YY.”

Unless defined otherwise, all technical and scientific terms used herein have the same meanings as commonly understood by one of ordinary skill in the art to which this invention belongs. Although any methods and materials similar or equivalent to those described herein can be used in the practice or testing of the present invention, the preferred methods and materials are now described. Nothing herein is to be construed as an admission that the invention is not entitled to antedate such disclosure by virtue of prior invention.

Whenever a range is given in the specification, for example, a temperature range, a time range, or a composition or concentration range, all intermediate ranges and subranges, as well as all individual values included in the ranges given are intended to be included in the disclosure. As used herein, ranges specifically include the values provided as endpoint values of the range. For example, a range of 1 to 100 specifically includes the end point values of 1 and 100. It will be understood that any subranges or individual values in a range or subrange that are included in the description herein can be excluded from the claims herein.

As used herein, “comprising” is synonymous with “including,” “containing,” or “characterized by,” and is inclusive or open-ended and does not exclude additional, unrecited elements or method steps. As used herein, “consisting of” excludes any element, step, or ingredient not specified in the claim element. As used herein, “consisting essentially of” does not exclude materials or steps that do not materially affect the basic and novel characteristics of the claim. In each instance herein any of the terms “comprising”, “consisting essentially of” and “consisting of” may be replaced with either of the other two terms.

One of ordinary skill in the art will appreciate that starting materials, biological materials, reagents, synthetic methods, purification methods, analytical methods, assay methods, and biological methods other than those specifically exemplified can be employed in the practice of the invention without resort to undue experimentation. All art-known functional equivalents, of any such materials and methods are intended to be included in this invention. The terms and expressions which have been employed are used as terms of description and not of limitation, and there is no intention that in the use of such terms and expressions of excluding any equivalents of the features shown and described or portions thereof, but it is recognized that various modifications are possible within the scope of the invention claimed. Thus, it should be understood that although the present invention has been specifically disclosed by preferred embodiments and optional features, modification and variation of the concepts herein disclosed may be resorted to by those skilled in the art, and that such modifications and variations are considered to be within the scope of this invention as defined by the appended claims. 

1-115. (canceled)
 116. A self-assembled polymer structure comprising: a plurality of graft block copolymers, each graft block copolymer independently comprising at least a first polymer block and a second polymer block; wherein: the first polymer block of each graft block copolymer comprises a first backbone and the second polymer block comprises a second backbone, the first backbone being directly or indirectly covalently linked to the second backbone; the first polymer block comprises at least 10 first repeating units; each of said first repeating units comprising a first polymer backbone group and directly or indirectly covalently linked to a first polymer side chain group; the first polymer block further comprises a first diluent group incorporated into the first backbone provided in an amount such that the first polymer block is characterized by a preselected first graft density of said first repeating units.
 117. The structure of claim 116 being a polymer network.
 118. The structure of claim 116 comprising polymer side chains capable of cross linking polymers.
 119. The structure of claim 116, wherein the preselected first graft density is selected from the range of 0.001 to 0.999.
 120. The structure of claim 119, wherein the second polymer block is characterized by a second graft density; and wherein the second graft density is selected from the range of greater than 0 to 1.0.
 121. The structure of claim 116, wherein the second polymer block of each graft block copolymer comprises: at least 10 second repeating units; each of said second repeating units comprising a second polymer backbone group and directly or indirectly covalently linked to a second polymer side chain group; and a second diluent group incorporated into the second backbone provided in an amount such that the second polymer block is characterized by a preselected second graft density of said second repeating units; wherein: the second polymer side chain group is different from the first polymer side chain group; and said second diluent group is different from said first diluent group.
 122. The structure of claim 121, wherein the preselected second graft density is selected from the range of 0.001 to 0.999.
 123. The structure of claim 116, wherein the first polymer block of each graft copolymer is further characterized by a preselected first graft distribution of said first repeating units; and wherein the preselected first graft distribution is an alternating graft distribution, a blocky graft distribution, a random graft distribution, a linearly gradient graft distribution, or a non-linearly gradient graft distribution.
 124. The structure of claim 121, wherein the second polymer block of each graft copolymer is further characterized by a preselected second graft distribution of said second repeating units; and wherein the preselected second graft distribution is an alternating graft distribution, a blocky graft distribution, a random graft distribution, a linearly gradient graft distribution, or a non-linearly gradient graft distribution.
 125. The structure of claim 116 being a lamellar structure, a matrix-sphere structure, a matrix-cylinder structure, or a matrix-gyroid structure.
 126. The structure of claim 125 being a lamellar structure having a periodicity selected from the range of 20 nm to 400 nm.
 127. The structure of claim 125 being a lamellar structure having a total thickness in a transverse direction selected from the range of 40 nm to 1400 nm.
 128. The structure of claim 116 being a coating.
 129. The structure of claim 116 being at least partially configured as a photonic crystal.
 130. The structure of claim 129, wherein said photonic crystal is configured to reflect at least a portion of wavelengths of the visible light spectrum, at least a portion of wavelengths of the infrared light spectrum, or at least a portion of wavelengths of the visible light spectrum and of the infrared light spectrum.
 131. The structure of claim 116 being configured as: a transmissive surface coating, configured to transmit at least a portion of visible light; a partially reflective surface coating, configured to reflect at least a portion of visible light; a photonic crystal; a solid polymer electrolyte; a scaffold for growth of biological materials; scaffold for controlling nanoadditive distribution or orientation; a gradient mechanical property structure; or a combination thereof.
 132. The structure of claim 116 being an annealed polymer network.
 133. The structure of claim 116 being a polymer network characterized by a degree of crystallinity selected from the range of 10% to 90%.
 134. The structure of claim 116, comprising thermosensitive graft block copolymers or graft block copolymers having thermosensitive groups.
 135. The structure of claim 116, wherein a polydispersity index of each graft block copolymer is selected from the range of 1.00 to 1.30.
 136. The structure of claim 116, wherein the first polymer block of each graft copolymer is characterized by a first degree of polymerization of the first repeating units, the first degree of polymerization being selected from the range of 10 to
 1000. 137. The structure of claim 121, wherein the second polymer block of each graft copolymer is characterized by a second degree of polymerization of the second repeating units, the second degree of polymerization being selected from the range of 10 to
 1000. 138. The structure of claim 116, wherein each of the first repeating units is independently defined by the formula (FX10a), (FX10b), (FX10c), (FX11d), (FX11e), (FX11f), (FX11g), (FX11h), or (FX11i):

wherein: B² is the first backbone group; each A¹ is independently an anchor group having the formula (FX3a) or (FX3b):

each L¹ is independently a linker group selected from the group consisting of a single bond, —O—, C₁-C₁₀ alkyl, C₂-C₁₀ alkenylene, C₃-C₁₀ arylene, C₁-C₁₀ alkoxy, C₁-C₁₀ acyl, triazole, diazole, pyrazole, and any combination thereof; and each P¹ is independently the first polymer side chain group.
 139. The structure of claim 138, wherein each of the first diluent groups is independently defined by the formula (FX11a), (FX11b), (FX11c), (FX11d), (FX11e), (FX11f), (FX11g), (FX11h), or (FX11i):

wherein: B² is the first backbone group; each A¹ is independently an anchor group having the formula (FX3a) or (FX3b):

each L¹ is independently a linker group selected from the group consisting of a single bond, —O—, C₁-C₁₀ alkyl, C₂-C₁₀ alkenylene, C₃-C₁₀ arylene, C₁-C₁₀ alkoxy, C₁-C₁₀ acyl, triazole, diazole, pyrazole, and any combination thereof; and each D¹ is independently a dangling group that is a substituted or unsubstituted C₁-C₃₀ alkyl, C₃-C₃₀ cycloalkyl, C₅-C₃₀ aryl, C₅-C₃₀ heteroaryl, C₁-C₃₀ acyl, C₁-C₃₀ hydroxyl, C₁-C₃₀ alkoxy, C₂-C₃₀ alkenyl, C₂-C₃₀ alkynyl, C₅-C₃₀ alkylaryl, —CO₂R³, —CONR⁴R⁵, —COR⁶, —SOR⁷, —OSR⁸, —SO₂R⁹, —OR¹⁰, —SR¹¹, —NR¹²R¹³, —NR¹⁴COR¹⁵, C₁-C₃₀ alkyl halide, phosphonate, phosphonic acid, silane, siloxane, silsesquioxane, C₂-C₃₀ halocarbon chain, C₂-C₃₀ perfluorocarbon, C₂-C₃₀ polyethylene glycol, a metal, or a metal complex; and wherein each of R³-R¹⁵ is independently H, C₅-C₁₀ aryl or C₁-C₁₀ alkyl. 